TW200927990A - High tensile strength galvanized steel sheet excellent in workability and method for manufacturing the same - Google Patents

High tensile strength galvanized steel sheet excellent in workability and method for manufacturing the same Download PDF

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Publication number
TW200927990A
TW200927990A TW097140611A TW97140611A TW200927990A TW 200927990 A TW200927990 A TW 200927990A TW 097140611 A TW097140611 A TW 097140611A TW 97140611 A TW97140611 A TW 97140611A TW 200927990 A TW200927990 A TW 200927990A
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Taiwan
Prior art keywords
iron
strength
steel sheet
temperature
zinc
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TW097140611A
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Chinese (zh)
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TWI406966B (en
Inventor
Tatsuya Nakagaito
Shusaku Takagi
Saiji Matsuoka
Shinjiro Kaneko
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Jfe Steel Corp
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Priority claimed from JP2007277040A external-priority patent/JP5256690B2/en
Priority claimed from JP2007277039A external-priority patent/JP5256689B2/en
Application filed by Jfe Steel Corp filed Critical Jfe Steel Corp
Publication of TW200927990A publication Critical patent/TW200927990A/en
Application granted granted Critical
Publication of TWI406966B publication Critical patent/TWI406966B/en

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    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0426—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
    • C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
    • C21D8/0436—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/005—Ferrite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/12—All metal or with adjacent metals
    • Y10T428/12493—Composite; i.e., plural, adjacent, spatially distinct metal components [e.g., layers, joint, etc.]
    • Y10T428/12771—Transition metal-base component
    • Y10T428/12785—Group IIB metal-base component
    • Y10T428/12792—Zn-base component
    • Y10T428/12799—Next to Fe-base component [e.g., galvanized]

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Coating With Molten Metal (AREA)

Abstract

The invention provides a high-strength hot-dip zinc plated steel sheet which exhibits high TS-El balance, excellent stretch frangeability, excellent workability due to low YR, and excellent impact characteristics, and a process for manufacturing the same. A high-strength hot-dip zinc plated steel sheet excellent in workability and impact characteristics, having a composition which contains by mass C: 0.05 to 0.3%, Si: 0.01 to 2.5%, Mn: 0.5 to 3.5%, P: 0.003 to 0.100%, S: 0.02% or below, Al: 0.010 to 1.5%, and N: 0.007% or below and further contains at least one element selected from among Ti, Nb and V in a total amount of 0.01 to 0.2% with the balance being Fe and unavoidable impurities and a microstructure which comprises, in terms of area fraction, 20 to 87% of ferrite, 3 to 10% (in total) of martensite and retained austenite, and 10 to 60% of tempered martensite and in which the average grain diameter of the second phase consisting of the martensite, retained austenite, and tempered martensite is 3[mu]m or below.

Description

200927990 六、發明說明： 【發明所屬之技術領域】 關於使用於汽車、電氣等產業領域之加工性及耐 之高強纽融錢鋅鋼板及其製造方法。 正:IS要1保護地球核境的觀點而言’汽車之燃料費增長 化==因此，將屬於車體材料之鋼板進行高強度 ㈣之餘量化的㈣變得活躍。由於車體 ==化與汽車衝突時之安全性提升相關，故高強度 鋼板被積極推展應用於車體材L，-般而言，由於鋼 板之南強度化會導致鋼板之延展性降低、亦即加讀降低， 故期望有兼具高強度與高加工性，且耐触亦優越之熔融鐘 鋅鋼板。 對於此期待，迄今已開發有由肥粒鐵與麻田散鐵所形成之 ❹DP(Dual Phase，雙相）鋼或利用了殘留沃斯田鐵之變態致塑 性的 TRIP(Transformation Induced Plasticity)鋼等的複 合組織型之高強度熔融鍍鋅鋼板。 於非專利文獻1中，揭示有肥粒鐵-麻田散鐵2相組織鋼200927990 VI. Description of the invention: [Technical field to which the invention pertains] Processability and resistance to high-strength Newcomb zinc steel sheets used in the automotive, electrical and other industrial fields and their manufacturing methods. In the case of the stipulations of the stipulations of the stipulations of the stipulations of the stipulations of the stipulations of the stipulations of the sth. Since the body=== is related to the safety improvement in the car conflict, the high-strength steel plate is actively applied to the car body L. In general, the ductility of the steel plate is lowered due to the south strength of the steel plate. That is, the addition of the reading is lowered, so that it is desired to have a high-strength and high-processability, and the melt-resistant zinc steel sheet which is superior in touch resistance. In response to this expectation, ❹DP (Dual Phase) steel formed by ferrite iron and 麻田散铁 or TRIP (Transformation Induced Plasticity) steel which utilizes metamorphic plasticity of residual Worthite iron has been developed so far. High-strength hot-dip galvanized steel sheet of composite structure type. In Non-Patent Document 1, it is disclosed that there is a ferrite iron-Mita loose iron 2-phase microstructure steel.

P 顯示優異之对衝擊特性。然而’肥粒鐵-麻田散鐵2相組織 鋼係r值未滿1. 〇，深衝（deep drawing)性低，故可應用之 領域有所限定。 專利文獻1中，提案有一種加工性優良之高強度合金化熔 097140611 3 200927990 融鍍鋅鋼板，係以質量％計含有C : 0. 05〜0. 15%、Si · 0. 3〜1. 5%、Μη : 1. 5〜2. 8%、P : 0. 03%以下、S : 0. 〇2%以下 Α1 : 0· 005〜〇· 5%、Ν : 〇. 0060%以下、剩餘部分為Fe及不可 - 避免之雜質，再者，滿足（Mn%)/(C%)215且 -4，肥粒鐵中含有以體積率計之3〜20%的麻田散鐵與殘留= 斯田鐵。然而，此種複合組織型之高強度熔融鍍鋅鋼板，雖 然以單軸拉伸所求取之伸展E1較高，但有擴孔加工等所需 ❹之伸展凸緣性（Stretch flangeability)差劣的問題。 因此’專利文獻2揭示有一種伸展凸緣性優越之高強度熔 融鍍鋅鋼板之製造方法，係將以質量％計含有 〇. 02〜0· 30%、Si : l 50%以下、Mn : 〇. 6(M 〇%、p : 〇 ⑽ 以下、S : 〇. 05%以下、A1 : 〇. 〇1〜〇. 1〇%、剩餘部為pe及不0 可避免之雜質的鋼，以Acs變態點以上進行熱軋後，予以酸 洗、冷軋，在連續回火熔融鍍鋅鋼板生產線中，加熱保持為 ❹再結晶溫度以上且，其後，在抵達炫融錢鋅 浴為止的期間，急冷至⑹點以下，於鋼板中生成部分或全 部之麻田散鐵，接著，加熱至Ms點以上之溫度的至少_ 贿祕歧合金铺財，卿科性或全雜回火，生 成麻田散鐵。 非專利文獻1:「鐵與鋼」，v〇l 83(1997)p748 專利文獻1:日本專利特開平11-279691號公報 專利文獻2·日本專利特開平6、9334〇號公報 097140611 4 200927990 【發明内容】 :::===-，一異 ㈣E1之積、亦即ts-E1平衡較 7取之拉伸強度 ys與ts之比的降伏比叫Ys=^問題。並有降伏強度 題。又，存在有對汽車衝突時 ㈣的問 特性差劣的_。 ^所必要之耐衝擊 異H目Γ繼—㈣询衡高、伸展凸緣性優 、 "工&優異的的纽崎鋅鋼板及其之製 造方法。又，本發明之目的在於提供一種TS-E1平衡高、伸 展凸緣性優異、且耐衝擊躲優異的高強歧融鍍鋅鋼板及 其之製造方法。 本發明者等人針對TS_E1平衡高（具體而言為TSXE1g 19000MPa· %)、伸展凸緣性優異（具體而言為後述之擴孔率 ❹又$ 7〇/〇且YR低（具體而言為yr< 75%)之加工性優異的高 強度熔融鍍鋅鋼板進行潛心研究，結果發現以下情事。 i)將成分組成適當化後’藉由作成以面積率計含有肥粒鐵 20〜87%、麻田散鐵與殘留沃斯田鐵合計3〜1〇%、回火麻田散 鐵10〜60%的微組織，則不僅是優異之伸展凸緣性，亦可達 成咼TS-E1平衡與低伙。 ii)此種微組織，係藉由在回火時自750〜950°C之加熱溫 度強制冷卻至（Ms點-i〇〇°C)〜（Ms點-200°C)之溫度區域，其 097140611 5 200927990 後進行再加執 實施溶一鍍鋅所獲得。於此，Ms點係指 自沃斯田鐵開始蠻 雙4為麻田散鐵的溫度，可由冷卻時之鋼之 線膨脹係數的變化求取。 古 係、根據此種見解而形成者，提供一種加工性優異之 炼融錢辞鋼板，其具有以質量％計含有C : 0.05~0.3°/〇>Si：n m , • υι~2. 5%>Μη： 0. 5~3. 5%>Ρ： 0. 003-0. 100%' S : 0. 02%以下、Α1 . ΛP shows excellent impact characteristics. However, the 'fertilizer iron-Mita loose iron 2-phase structure steel system r value is less than 1. 〇, deep drawing is low, so the applicable field is limited. 〜1. 3〜1. In the case of the high-strength alloyed refractory 097140611 3 200927990 fused galvanized steel sheet, C: 0. 05~0. 15%, Si · 0. 3~1. 5%, Μη: 1. 5~2. 8%, P: 0. 03% or less, S: 0. 〇2% or less Α1: 0· 005~〇· 5%, Ν: 〇. 0060% or less, remaining Some are Fe and non-avoidable impurities, and further, satisfy (Mn%) / (C%) 215 and -4, and the ferrite iron contains 3 to 20% of the volume of the granulated iron and the residue = s Tian Tie. However, in the high-strength hot-dip galvanized steel sheet of the composite structure type, although the elongation E1 obtained by the uniaxial stretching is high, the stretch flangeability of the crucible required for the reaming processing or the like is inferior. The problem. Therefore, Patent Document 2 discloses a method for producing a high-strength hot-dip galvanized steel sheet having excellent stretch flangeability, which is contained in mass% of 〇. 02~0·30%, Si: l 50% or less, Mn: 〇 6(M 〇%, p : 〇(10) or less, S : 〇. 05% or less, A1 : 〇. 〇1~〇. 1〇%, the remaining part is pe and the steel which is not zero avoidable impurities, to Acs After the hot rolling is performed at an abnormal point or higher, it is pickled and cold-rolled, and in the continuous tempering hot-dip galvanized steel sheet production line, the heating is maintained at a temperature equal to or higher than the recrystallization temperature, and thereafter, after reaching the dazzling and melting zinc bath, Quenching to below (6) point, some or all of the granulated iron in the steel plate is formed, and then heated to at least the temperature above the Ms point _ bribe secret alloy deposits, Qingke or full misfire, to form the granulated iron Non-Patent Document 1: "Iron and Steel", v〇l 83 (1997) p748 Patent Document 1: Japanese Patent Laid-Open No. Hei 11-279691, Patent Document 2, Japanese Patent Laid-Open No. Hei No. 6, No. 9334 No. 097140611 4 200927990 [Summary] :::===-, the product of a different (four) E1, that is, the balance of ts-E1 is stronger than that of 7 The ratio of the ratio of ys to ts is called Ys=^. There is a problem of the strength of the fall. In addition, there is a problem with the characteristics of the car conflict (4) _. ^ The necessary impact resistance is different from the H--(4) A high-strength, stretch-flange excellent, "good & excellent  Nusaki zinc steel sheet and its manufacturing method. Further, it is an object of the present invention to provide a TS-E1 with high balance and excellent stretch flangeability, and The inventors of the present invention have a high balance of TS_E1 (specifically, TSXE1g 19000 MPa·%) and excellent stretch flangeability (specifically, expansion as described later). The high-strength hot-dip galvanized steel sheet with excellent porosity and high YR (specifically yr< 75%) has been studied for the following problems. The results are as follows: i) After the composition of the components is optimized 'It is not only excellent by making 20~87% of ferrite iron in area ratio, 3~1〇% of 麻田散铁 and residual Worthite iron, and 10~60% of tempered granita iron. The stretch flangeability can also achieve 咼TS-E1 balance and low ii. ii) such micro-structure, By forced cooling from 750 to 950 ° C during tempering to a temperature range of (Ms point - i 〇〇 ° C) ~ (Ms point - 200 ° C), which is added after 097140611 5 200927990 Obtained by the implementation of dissolution-zinc plating. Here, the Ms point refers to the temperature from the Vostian Iron, which is the temperature of the blasting iron, which can be obtained from the change of the linear expansion coefficient of the steel during cooling. The ancient system, which is formed by such a viewpoint, provides a refining and refining steel sheet having excellent workability, which has C: 0.05 to 0.3 ° / 〇 > Si: nm in mass %, • υι~2. 5 %>Μη: 0. 5~3. 5%>Ρ: 0. 003-0. 100%' S : 0. 02% or less, Α1. Λ

Ai . 01(Μ· 5%、Μ : 0. 007%以下，剩餘部Ai . 01 (Μ· 5%, Μ: 0. 007% or less, the remaining part

e $可避免之雜質的成分組成，且具有以面積率計含 有肥粒鐵2G〜87%、麻田散鐵與殘留沃斯田鐵合計3〜10%、回 火麻田散鐵1〇〜60%的微組織。 本發明之尚強度溶融鑛鋅鋼板中，視需要可進一步以質量 /〇e十含有選自 Cr : 〇. 〇〇5〜2. 00%、Mo : 0· 005〜2. 00%、V : 0. 005-2. 〇〇% > Ni ： 0. 005-2. 〇〇% > Cu ： 0. 005-2. 00%^j 1 m 或2種以上之元素。再者，視需要亦可進一步以質量％計含 有選自Τι : 〇· 〇1〜〇· 20%、Nb : 〇. 〇1〜〇. 20%的1種或2種以 上之兀素，或B: 〇. 〇〇〇2〜〇. 〇05%，或選自Ca: 〇· 〇〇1〜〇 〇〇5%、 REM : 0· 〇〇1〜〇. 005%的1種或2種以上之元素。 本發明之高強度熔融鍍鋅鋼板中，亦可將鑛辞設為合金化 鍍鋅。 本發明之高強度熔融鍍鋅鋼板，可例如藉由下述加工性優 異之高強度熔融鍍辞鋼板之製造方法而製造：將具有上述成 分組成之鋼链施行熱軋、冷軋而作成冷軋鋼板，以對上述冷 097140611 6 200927990 鋼T進仃加熱至75〇~95〇β。之溫度區域並保持以上 <。75m(rc/s以上之平均冷卻逮度冷卻至⑽點 C)〜⑽點⑼代）之溫度區域，再加熱至350〜議。C之 .溫度區域並保持卜_3之條件而實施回火後，施行溶融鐘 . 鋅。 本發明之而強度熔融鍍鋅鋼板之製造方法中，亦可於溶融 鍛鋅後’將鍍鋅進行合金化處理。 ❹ #由本^明’可製造TS-E1平衡高、伸展凸緣性優異、且 低之加工性優異的高強度熔融鑛鋅鋼板。藉由將本發明 之高強度炫融鍍鋅鋼板應用至汽車車體，财僅可達到汽車 之輕量化或耐蝕性提升，亦可達到衝突安全性之提升。 本發明者等人針對TS_E1平衡高（具體而言為取職 19000MPa · %)、伸展凸緣性優異（具體而言為後述之擴孔率 λ 2 50%)且耐衝擊雜亦優異（具體而言錢述之吸收能量 ❹ΑΕ肖TS之比AE/TS以.關之高強度您融錢鋅鋼板進行潛 心研究’結果發現以下情事。 iii)將成分組成適當化後，藉由作成以面積率計含有肥粒 • 鐵20~87%、麻田散鐵與殘留沃斯田鐵合計3〜10%、回火麻田 散鐵10〜60%，且含有麻田散鐵與殘留沃斯田鐵與回火麻田 散鐵的第二相之平均結晶粒徑為以下的微組織，則不 僅是優異之伸展凸緣性，亦可達成高TS〜E1平衡與優異之耐 衝擊特性。 μ 097140611 7 200927990 續姆:組織，係藉由在回火時於5〇〇。〇〜Aci變態點之e $ can avoid the composition of the impurities, and has 2G~87% of ferrite iron in the area ratio, 3~10% of the balance of the granulated iron and the residual Worthite, and 1~60% of the tempered granulated iron Micro organization. 00%, Mo: 0· 005~2. 00%, V: The 00%, Mo: 0· 005~2. 00%, V: 0. 005-2. 〇〇% > Ni : 0. 005-2. 〇〇% > Cu : 0. 005-2. 00%^j 1 m or more than two elements. Further, if necessary, it may further contain, in mass%, one or two or more kinds of halogen selected from the group consisting of Τι : 〇·〇1~〇·20%, Nb: 〇. 〇1~〇. 20%, or B: 〇. 〇〇〇2~〇. 〇05%, or selected from Ca: 〇· 〇〇1~〇〇〇5%, REM: 0· 〇〇1~〇. 005% of 1 or 2 The above elements. In the high-strength hot-dip galvanized steel sheet of the present invention, the ore can also be alloyed and galvanized. The high-strength hot-dip galvanized steel sheet according to the present invention can be produced, for example, by a method for producing a high-strength molten-plated steel sheet having excellent workability, wherein a steel chain having the above-described composition is hot-rolled and cold-rolled to be cold-rolled. The steel plate is heated to 75 〇 to 95 〇 β to the above-mentioned cold 097140611 6 200927990 steel T. The temperature zone and keep the above <. 75m (average cooling arrest above rc/s is cooled to (10) point C) ~ (10) point (9) generation) temperature zone, and then heated to 350~. After the tempering is carried out in the temperature zone and under the condition of maintaining the condition of _3, a melting clock is applied. Zinc. In the method for producing a high-strength hot-dip galvanized steel sheet according to the present invention, the galvanization may be subjected to alloying treatment after the molten zinc is melted. ❹ #由本明' can produce a high-strength molten zinc-zinc steel sheet with high balance of TS-E1, excellent stretch flangeability, and low workability. By applying the high-strength glazed galvanized steel sheet of the present invention to an automobile body, the finance can only achieve an increase in weight or corrosion resistance of the automobile, and can also achieve an increase in conflict safety. The inventors of the present invention have a high balance of TS_E1 (specifically, 19000 MPa · %), and excellent stretch flangeability (specifically, a hole expansion ratio λ 2 50% to be described later), and are excellent in impact resistance (specifically言 述 述 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸 吸Contains fat particles • Iron 20~87%, Ma Tian loose iron and residual Worth iron total 3~10%, tempered Ma Tian loose iron 10~60%, and contains Ma Tian loose iron and residual Worth iron and tempered Ma Tian When the average crystal grain size of the second phase of the loose iron is the following microstructure, not only the excellent stretch flangeability but also the high TS to E1 balance and excellent impact resistance can be achieved. μ 097140611 7 200927990 Continued: Organization, by 回 when tempered at 5 〇〇. 〇~Aci metamorphosis point

溫度區域从HTC/s以上之升溫速度進行升溫，加熱至Aci 變態點〜（A C3變態點+30°C)之溫度區域並保持1〇s以上，而 藉變態、& 。0 (M戍細微之沃斯田鐵後，強制冷卻至（心點-100 =Sl2GG°C)之溫度區域’其後進行再加熱，而實施 …3 ' 4所獲得。於此，Ms點係指自沃斯田鐵開始變態為 ❹ 參 麻田散鐵的溫度，可*冷卻時之鋼之線膨脹係數的變:求 取0 本發明係根據此種見解而形成者，提供一種加工性及耐衝 擊特性優異之高強度熔融鍍鋅鋼板，其具有以質量。% C · 0.05-0.3% ' Si ： 0.01-2.5% ' Μη ： Ο.5-3 〇· 003〜0· loo%、s : 0· 02%以下、A1 : 〇. oio〜]ςϋ/ ? *The temperature region is heated from a temperature increase rate of HTC/s or higher, and is heated to a temperature region of Aci metamorphosis point ~ (A C3 metamorphic point + 30 ° C) and maintained for more than 1 〇s, and the metamorphosis, & 0 (M 戍 戍 之 沃 沃 沃 , , , 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制 强制Refers to the temperature from the Vostian Iron to the temperature of the 散 麻 麻 散 散 , , , , , , 麻 麻 麻 冷却 冷却 冷却 : 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却 冷却High-strength hot-dip galvanized steel sheet with excellent impact properties, with mass % C · 0.05-0.3% ' Si : 0.01-2.5% ' Μ η : Ο.5-3 〇 · 003~0· loo%, s : 0 · 02% or less, A1 : 〇. oio~]ςϋ/ ? *

Nb及V之至少i種元素合計〇. 〇卜〇· 2%，剩餘部為ρ 1、 可避免之雜質的成分組成，且具有以面積率計含 及不 20〜87%、麻田散鐵與殘留沃斯田鐵合計3〜1⑽、 粒鐵 鐵10〜60%，而上述含有麻喊鐵與殘留沃斯^與麻田散 田散鐵的第二相之平均結晶粒徑為3_以下的微組回火麻 本發明之兩強度溶融鑛鋅鋼板中，視需要可進'、 %計含有選自（：1^ 0.005~2.00%、1^:0.005~9心步以質量 ^ ^ 0% Ν Μ ^ . 〇.〇〇5〜2.〇〇%、〇1:〇.005〜2.00%的1種或2種以上 . 再者，視需要亦可進一步以質量％計含有Β : 〇()Q2之7°素。 或選自 Ca : 〇. 〇〇1 〜〇. 005%、REM : 〇. 〇〇1 〜〇· 〇〇5%的 〇. 〇〇5% 種或2 097140611 8 200927990 種以上之元素。 本發明之高強度熔融鍍鋅鋼板中，亦可將鍍辞設為合金化 鑛鋅。 本發明之高強度熔融鍍鋅鋼板，可例如藉由下述製造方法 • 而製^.將具有上述成分組成之鋼链施行熱札、冷乾而作成 冷軋鋼板，以對上述冷軋鋼板，於50(rc〜Aci變態點之溫度 區域依10°C/s以上之平均升溫速度進行升溫，加熱至Aci ❹變態點〜（Ac3變態點+30。〇)之溫度區域並保持10s以上後， 以10C/s以上之平均冷卻速度冷卻至（Ms點_1⑽。 #_2〇〇°〇之$度區域’再加熱至35G〜6Q(rc之溫度區域並 吓河Α ϋυ心心條仵而實施回火後，施行熔融鍍鋅。The total of at least i elements of Nb and V 〇. 〇 〇 · 2%, the remaining part is ρ 1, the composition of impurities that can be avoided, and has an area ratio of not more than 20 to 87%, Ma Tian loose iron and Remaining Vostian iron total 3~1 (10), granular iron iron 10~60%, and the above micro-group containing the average phase crystal grain size of the second phase of the yoke iron and the residual Worth ^ and the granulated iron In the two-strength molten zinc-zinc steel plate of the invention, it can be selected as follows: (1^ 0.005~2.00%, 1^: 0.005~9 heart step by mass ^ ^ 0% Ν 中^ . 〇 〇〇 〜 〜 〜 〜 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 005 7°素. Or selected from Ca: 〇. 〇〇1 〇. 005%, REM: 〇. 〇〇1 〇〇· 〇〇5% 〇. 〇〇5% or 2 097140611 8 200927990 or more In the high-strength hot-dip galvanized steel sheet according to the present invention, the plating is also referred to as alloyed ore zinc. The high-strength hot-dip galvanized steel sheet of the present invention can be produced, for example, by the following manufacturing method. Having the above composition The steel chain is hot-rolled and cold-dried to form a cold-rolled steel sheet, and the temperature of the cold-rolled steel sheet is raised at an average temperature increase rate of 10 ° C/s or more in a temperature range of 50 (rc to Aci), and heated to Aci ❹ After the temperature point of the metamorphosis point ~ (Ac3 metamorphosis point +30. 〇) is maintained for more than 10 s, it is cooled to (Ms point _1 (10) at an average cooling rate of 10 C / s or more. #_2〇〇 °〇 $度区' After heating to 35G~6Q (the temperature zone of rc and tempering the heart and tempering, tempering is performed, and hot galvanizing is performed.

本發明之高強度熔融鍍鋅鋼板之製造方法中，亦可於熔融 鑛鋅後，㈣鋅崎合金化處理。 丨了於W ❹ 射fΪ本發明’可製造啊1平衡高、伸展凸緣性優異、且 ==:::高強〜鋅鋼板。藉由將二 量化或應:至汽車車雜，則不僅可達到汽車之輕 【實施方式】以升，亦可達到衝突安全性之提升。 又，表示成分元素之含量的「％」， 「質量％」。 以下，詳細說明本發明。 係在未特別限定之下意指 1)成分纟且4 C: 0.05〜% 097140611 9 200927990 c係使沃斯田鐵穩定化之元素，為用於使肥粒鐵以外之麻 田散鐵等第二相生成而提升TS、並提升TS-E1平衡所必要 的元素。若C量未滿〇. 05%，則難以峰保肥粒鐵以外之第二 -相，TS-E1平衡降低。另一方面，若c量超過0.3%，則熔接 • 性劣化。從而，C量設為0· 05〜0. 3%、較佳〇. 〇8〜〇. 15%。In the method for producing a high-strength hot-dip galvanized steel sheet according to the present invention, it may be subjected to (d) zinc-sinter alloying treatment after melting the ore. The invention can be manufactured by the invention, which is high in balance, excellent in stretch flangeability, and ==::: high strength ~ zinc steel plate. By quantifying or arranging: to the car, it can not only achieve the lightness of the car. [Embodiment] In the case of liters, it can also achieve the improvement of conflict safety. Further, "%" and "% by mass" of the content of the component elements are indicated. Hereinafter, the present invention will be described in detail. It is not specifically limited to mean 1) component 纟 and 4 C: 0.05% to 097140611 9 200927990 c is an element which stabilizes Worthite iron, and is used as a second element for making fertile iron other than the fertile iron. The phase is generated to enhance the TS and enhance the elements necessary for TS-E1 balance. If the amount of C is less than 〇. 05%, it is difficult to maintain the second phase other than the ferrite, and the balance of TS-E1 is lowered. On the other hand, if the amount of c exceeds 0.3%, the weldability deteriorates. Therefore, the amount of C is set to 0. 05~0. 3%, preferably 〇. 〇8~〇. 15%.

Si ： 0. 01-2. 5%Si : 0. 01-2. 5%

Si係有效地使鋼固溶強化，提升TS-E1平衡的元素。為 φ 了得到此種效果’必需將Si量設為〇· 〇1%以上。另一方面， 若Si量超過2. 5%，則導致E1降低或表面性狀、熔接性劣 化。從而，Si量設為〇· 01〜2. 5%、較佳〇 7〜2 〇%。 Μη ： 0. 5-3. 5% Μη係有效地進行鋼強化，並促進麻田散鐵等第二相生成 的元素。為了得到此種效果，必需將此量設為〇 5%以上。 另一方面，若Μη量超過3.5%，則第二相過剩地增加或因固 ❹溶強化所造成之肥粒鐵之延展性劣化變得顯著，加工性降 低。從而，Μη量設為〇. 5〜3· 5%、較佳l 5〜3, 。 Ρ · 0. 003-0. 100% Ρ係有效地進行_化的元素。為了㈣此種效果，必需 將Ρ量設為0.003%以上。另-方面，若ρ量超過〇.圃， 則因粒界偏析而使鋼脆化，耐衝擊特性劣化。從而，ρ量設 為 0. 003〜0. 100%。 S : 0· 02%以下 097140611 10 200927990 S係以MnS等之介存物之型式存在，由於其使耐衝擊特性 或熔接时化’故較佳係極力減低其含量。㈣，由製造成 本方面而言，S量設為〇. 〇2%以下。 . A1 : 〇. 010〜1. 5% . A1係使肥粒鐵生成，有效提升TS-E1平衡的元素。為了 得到此種效果，必需將A1量設為〇. 〇1〇%以上。另一方面， 若A1量超過1. 5%，則於連續鑄造時之鋼坯破裂之危險性提 ❹ 高。從而，A1量設為〇. oloq. 5%。 N : 0. 007%以下 N係使鋼之耐時效性劣化的元素。若N量超過〇. 〇〇7%，則 耐叫·效性顯者劣化。從而，N量設為〇. 007%以下，但越少越 好。 選自Ti、Nb及V之至少1種：合計〇. 〇1〜〇. 2%The Si system effectively solidifies steel and enhances the element of TS-E1 balance. It is necessary to obtain such an effect for φ. It is necessary to set the amount of Si to 〇·〇1% or more. On the other hand, when the amount of Si exceeds 2.5%, E1 is lowered, surface properties, and weldability are deteriorated. Therefore, the amount of Si is set to 〇· 01 to 2.5%, preferably 〜 7 to 2 〇%. Μη : 0. 5-3. 5% Μ 系 is effective for steel strengthening and promotes elements produced by the second phase such as the granulated iron. In order to obtain such an effect, it is necessary to set this amount to 〇 5% or more. On the other hand, when the amount of Μη exceeds 3.5%, the second phase is excessively increased or the ductility deterioration of the ferrite iron due to solid solution strengthening is remarkable, and the workability is lowered. Therefore, the amount of Μη is set to 〇. 5~3· 5%, preferably l 5~3, . Ρ · 0. 003-0. 100% Ρ is an element that is effectively _. In order to (4) such an effect, it is necessary to set the amount of enthalpy to 0.003% or more. On the other hand, when the amount of ρ exceeds 〇.圃, the steel is embrittled due to grain boundary segregation, and the impact resistance characteristics are deteriorated. Thus, the amount of ρ is set to 0. 003~0. 100%. S: 0·02% or less 097140611 10 200927990 S is in the form of a deposit of MnS or the like, and it is preferable to reduce the content by the impact resistance or the welding. (4) In terms of manufacturing cost, the amount of S is set to 〇. 〇 2% or less. A1 : 〇. 010~1. 5% . A1 is an element that produces ferrite and iron and effectively raises the balance of TS-E1. In order to obtain such an effect, it is necessary to set the amount of A1 to 〇.〇1〇% or more. On the other hand, if the amount of A1 exceeds 1.5%, the risk of rupture of the slab during continuous casting is improved. Thus, the amount of A1 is set to 〇. oloq. 5%. N: 0. 007% or less N is an element which deteriorates the aging resistance of steel. If the amount of N exceeds 〇. 〇〇7%, the resistance and effectiveness are deteriorated. Therefore, the amount of N is set to 〇. 007% or less, but the less the better. At least one selected from the group consisting of Ti, Nb and V: total 〇. 〇1~〇. 2%

Ti、Nb及V係分別以TiC、NbC、VC等析出，有效地使鋼 ❿ 之組織細微化的元素。為了得到此種效果，必需將選自Ti、 Nb及V之至少1種元素之含量合計設為〇. 〇1%以上。另一方 面’若選自Ti、Nb及V之至少1種元素之含量合計超過 0· 2%，則析出物過剩’導致延展性降低。從而，選自Ti、 Nb及V之至少1種元素之含量合計設為〇. 〇i〜〇. 2%。 剩餘部雖為Fe及不可避免之雜質，但由以下理由，視需 要亦可含有 Cr : 0. 005〜2. 00%、Mo : 〇. 〇〇5〜2. 00%、V : 0. 005〜2. 00%、Ni : 0· 005〜2. 00%、Cu : 〇. 〇〇5~2. 00%、Ti : 097140611 11 200927990 ο. 〇l~0. 20% ' Nb ： 0. 01~0. 20% ' B ： 0. 0002-0. 005% ' Ca ： 〇· 〇(H〜0· 005%、REM : 0. 001 〜0. 005%。Ti, Nb, and V are elements which are precipitated by TiC, NbC, VC, etc., respectively, to effectively make the structure of the steel crucible fine. In order to obtain such an effect, it is necessary to set the total content of at least one element selected from the group consisting of Ti, Nb, and V to 〇1% or more. On the other hand, when the total content of at least one element selected from the group consisting of Ti, Nb and V exceeds 0.2%, the excess precipitates cause a decrease in ductility. Therefore, the total content of at least one element selected from the group consisting of Ti, Nb, and V is 〇. 〇i~〇. 2%. 00%, V: 0. 005. 00%, :5~2. 00%, V: 0. 005, the remaining part is Fe and unavoidable impurities, but may also contain Cr: 0. 005~2. 00%, Mo: 〇. 〇〇5~2. 00%, V: 0. 005 〜2. 00%, Ni: 0· 005~2. 00%, Cu: 〇. 〇〇5~2. 00%, Ti: 097140611 11 200927990 ο. 〇l~0. 20% ' Nb : 0. 01 ~0. 20% ' B : 0. 0002-0. 005% ' Ca : 〇· 〇 (H~0· 005%, REM: 0. 001 ~0. 005%.

Cr、Mo、v、Ni、Cu :分別為 0. 005〜2. 00% . 係在自回火時之加熱溫度進行冷卻時， • 抑制波來鐵生成，有效促進麻田散鐵等生成而使鋼強化的元 素為了得到此種效果，必需將選自Cr、Mo、V、N i、Cu 之至少1種元素之含量設為〇. 〇〇5%。另一方面，若Cr、Mo、 O V、Nl、cu之各元素含量超過2. 00%，則其效果飽和，導致 成本增力。。從而，Cr、Mo、V、Ni、Cu之含量分別設為 0·005~2._。Cr, Mo, v, Ni, and Cu: 0. 005~2. 00% . When cooling at the heating temperature at the time of self-tempering, • suppresses the generation of iron from the wave, and effectively promotes the formation of iron and the like in the field. In order to obtain such an effect, it is necessary to set the content of at least one element selected from the group consisting of Cr, Mo, V, N i and Cu to 〇. 〇〇 5%. On the other hand, if the content of each element of Cr, Mo, O V, Nl, and cu exceeds 2.0%, the effect is saturated, resulting in cost increase. . Therefore, the contents of Cr, Mo, V, Ni, and Cu are each set to 0·005 to 2..

Ti > Nh · \ D •分別為0. 01〜0. 20% T i Μ 1 b係形成碳氮化物，藉由鋼之析出強化而有效地進 行同強度化的元素。為了得到此種效果，必需將選自Ti、 Nb 1 ^ ^ p 夕1種元素之含量設為〇. 01%以上。另一方面，右* ❹ 1 Nb <各元素含量超過0. 20%，則過度高強度化，延展性 降低從而，Ti、Nb之含量分別設為〇 〇1~〇 2〇%。 B: 0.00〇2〜〇.005% • ''抑制自沃斯田鐵粒界的肥粒鐵生成，有效地使麻田散 〜相生成而達到高強度化的元素。為了得到此種效 果必需將B量設為〇. 0002%以上。另一方面，若β量超過 ，則其效果飽和，導致成本增加。從而，β量設為 〇.0002-g·〇05%。 097140611 12 200927990Ti > Nh · \ D • 0. 01~0. 20% T i Μ 1 b is an element which forms a carbonitride and is effectively strengthened by precipitation strengthening of steel. In order to obtain such an effect, it is necessary to set the content of one element selected from the group consisting of Ti and Nb 1 ^ ^ p to 0.01% or more. On the other hand, the right * ❹ 1 Nb < the content of each element exceeds 0.20%, the excessively high strength, and the ductility are lowered, and the contents of Ti and Nb are respectively set to 〇 〇1 to 〇 2〇%. B: 0.00〇2~〇.005% • ''Inhibition of the formation of fertilized iron from the iron field of the Worth, effectively stimulating the formation of the phase to form a high-strength element. In order to obtain such an effect, the amount of B must be set to 0002. 0002% or more. On the other hand, if the amount of β exceeds, the effect is saturated, resulting in an increase in cost. Therefore, the amount of β is set to 0002.0002-g·〇05%. 097140611 12 200927990

Ca、REM :分別為 〇. 001 〜〇· 005%Ca, REM: 〇. 001 ~ 〇 · 005%

Ca、REM任一者係藉由控制硫化物之形態，而有效地改善 加工性的元素。為了得到此種效果，必需將選自Ca、REM 之至少1種元素之含量设為〇. 001%以上。另一方面，若Ca、 REM各元素之含量超過0. 005%’則有對鋼之清潔度造成不良 影響之虞。從而，Ca、REM量分別設為〇. 〇〇1〜〇. 〇〇5%。 2)微組織Any of Ca and REM is an element which effectively improves the workability by controlling the form of the sulfide. In order to obtain such an effect, it is necessary to set the content of at least one element selected from the group consisting of Ca and REM to 0.001% or more. On the other hand, if the content of each element of Ca and REM exceeds 0.005%, there is a problem that the cleanliness of steel is adversely affected. Therefore, the amounts of Ca and REM are respectively set to 〇. 〇〇1 to 〇. 〇〇5%. 2) Micro organization

肥粒鐵之面積率：20〜87% 肥粒鐵係提升TS-E1平衡。於設為TSxE1^19()_pa · % 時，必須使肥粒鐵之面積率為2〇%以上、較佳通以上。又， 由於以下之細散鐵賤留沃斯喊之面積率合計為⑽以 上及回火麻田散鐵之面積率為⑽以上，故肥粒鐵的面積率 之上限為87%。 麻田散鐵與殘留沃斯田鐵之面積率：合計3〜廳 麻田散鐵與殘留沃斯田鐵不僅有助於鋼之強化 ，亦提升 平衡又’使YR降低。為了得到此種效果，麻田散 鐵與殘留沃斯田鐵之面積率必須合計為綱上。然而，若 麻田散鐵_留_喊之_率合計超過 10%，^伸展凸 心’麻田散鐵與殘留沃斯田鐵之面積率合計設 為3〜10%。 回火麻田散鐵之面積率 叫切干.ιυ〜ΰ〇%Area ratio of fertilized iron: 20~87% Fertilizer iron system improves TS-E1 balance. When TSxE1^19()_pa · % is used, the area ratio of the ferrite iron must be 2% or more, preferably more than or equal to. In addition, since the area ratio of the following fine iron 贱 沃 沃 喊 喊 合 ( ( ( ( ( ( 10 10 10 10 10 10 10 10 10 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻Area ratio of Ma Tian loose iron and residual Worth Tin: Total 3~ Hall Ma Tian loose iron and residual Worth iron not only contribute to steel reinforcement, but also improve balance and reduce YR. In order to achieve this effect, the area ratio of the granulated iron and the residual Worth iron must be combined. However, if the total amount of 麻田散铁_留_叫__ is more than 10%, the area ratio of the stretched convex heart and the residual Worth iron is set to 3~10%. The area ratio of tempered granulated iron is called cut dry. ιυ~ΰ〇%

回火麻田散鐵士 M :相較於回火前之麻田散鐵與殘留沃斯 097140611 13 200927990 並為有致建Tempered Ma Tian Shi Tieshi M: Compared to the tempering of the Ma Tian loose iron and residual Voss 097140611 13 200927990 and for the construction

60%，則無法得到TSx ‘建到高強度化之第二相。為了 1田散鐵之面積率為10%以上。 回火麻田散鐵之面積率設為 田鐵’其對伸展凸緣性之不良 之優越伸展凸緣性，並為有致」 得到此種效果，必需使回火麻 然而，若回火廠田勘雜夕 10〜60% 〇 影響較少，故可維持λ 250% 含有麻田散鐵與殘留沃斯田鐵與回火麻田散鐵的第二相 〇 之平均結晶粒徑：3μm以下 含有麻田散鐵與殘留沃斯田鐵與回火麻田散鐵的第二相 之存在，係有效作用於提升耐衝擊特性。尤其是使第二相之 平均結晶粒徑為3//m以下’可達成AE/TS20. 063。從而， 含有麻田散鐵與殘留沃斯田鐵與回火麻田散鐵的第二相之 平均結晶粒徑較佳為3"m以下。 尚且’作為麻田散鐵、殘留沃斯田鐵、回火麻田散鐵以外 ❹ 的第二相，亦可含有波來鐵或變韌鐵，但若滿足上述之肥粒 鐵、麻田散鐵、殘留沃斯田鐵、回火麻田散鐵之面積率或第 二相之平均結晶粒控，則玎達成本發明目的。又，由伸展凸 緣性之觀點而言，波來鐵之面積率較佳為3%以下。 於此’肥粒鐵、麻田散鐵、殘留沃斯田鐵、回火麻田散鐵 之面積率，係指各相於觀察面積中所佔有之面積比例，其可 藉由將鋼板之板厚剖面進行研磨後，以3%硝酸侵蝕液 (Nital)進行腐飯，以SEM(掃瞄電子顯微鏡）依1000〜3000 097140611 14 200927990 之倍率觀察板厚1/4之位置，使用市售之影像處理軟體而求 得。又，將含有麻田散鐵、殘留沃斯田鐵、回火麻田散鐵之 第二相之總面積除以第二相總個數，求取每—個第二相之不 均面積’將其平方根作為第二相之平均結晶粒捏。一 3)製造條件1 ❹ ❹ 本發明之高強度溶融鑛鋅鋼板，可藉由下述方法予以製 造：例如將具有上述成純成之鋼&施行減、冷軋而作成 冷軋鋼板’以對上述冷軋鋼板進行加熱至75q〜9阶之温度 區域並保持lGs以上後，自75代以1(rc/s以上之平^冷 部速度冷卻至（Ms 點 加熱至_ΐ之溫度區域並保持卜咖s之條件而實施 回火後，施行溶融鑛鋅。 回火時之加熱條件：於75()〜95(rc之溫度區域保持此以上 於回火時之加熱溫度為未滿75(rc或保持時間未滿此 時’沃斯_之生成不足，於其後之冷卻無法麵充分量之 麻田散鐵等第二相。又，若加熱溫度超過95Qt，則沃斯田 鐵粗化大’抑财料之肥粒鐵生成，而無法得到面積率 撤以上之肥粒鐵。從而，回火時之加熱係設為於75M5〇 f之溫度區域保持1〇s以上。保持時間之上限並無特別規 疋’即使進仃600s m持，其效果制鮮，導致成 本增加，故較佳係將保持時間設為未滿600s。 回火時之冷卻條件：自75代以耽/s以上之平均冷卻速 097140611 15 200927990 度m點儀MMs點讀） 加熱後，必須自750¾以l〇t/s以 坺 行冷卻，但若平均冷卻逮度未滿】〇t/之平均^卻速度進 鐵，無法得到所需量之回火麻田_S’則大量生成波來 田鐵。冷卻速度之上限雖並無⑼散鐵及殘留沃斯 化、難以將冷卻控制在（MS點-⑽。c)^ ’但由於鋼板形狀惡 ❹ 停止溫度區域，故較佳係設為2〇〇t/s以3下點之冷卻 度係控制其後之再加執 。冷較停止溫 所…府…熔嘁鍍鋅、鍍敷相之合金化處理時 斤生成之麻田散鐵、殘留沃斯田鐵、回 ^ 為本發明最重要的條件之—n鐵之篁，而 鐵與未變態輯輯之量，於其後之;;7止時蚊麻田散 為回火麻田散_，|_ ”、、、、<理中’麻田散鐵成 _，左顯為細散鐵或_沃斯 阳鐵左右者鋼強度、 1 卻之停止严声相、A, 展凸緣性、YR。若冷 ❹ 去繳能 點―100。0,則麻田散鐵變綠不；？ 未變態沃斯田鐵之番证 罈變態不足， 面積率合計超過10〇/ ^ 散鐵與殘留沃斯田鐵之 停止溫度未滿 散鐵，未變離、_ 斯田鐵幾乎變態為麻田 ，天斯田鐵之量變少，最終 田鐵之面積率合計未 ㈣夭斯 從而，回火平衡劣化，YR增加。 冷卻速度冷依自75mrc/s以上之平均 的條件進行。 orc)〜（Ms點~200。〇之溫度區域 097140611 16 200927990 回火時之再加熱條件：於35〇〜6〇(rc之溫度區域保持 1〜600s 以10 C/s以上之平均冷卻速度冷卻至⑽點一議。c 點-2〇〇。〇之溫度區域後，藉由進行於湖〜之溫度區 域雜is以上之再加熱，可料卻時所生紅麻田散鐵進 行回火纟成面積率10〜60%之回火麻田散鐵，可維持優異 之伸展凸緣性並達成高強度化。若再加熱溫度未滿 350°C 或 /、寺夺門未滿Is ’則回火麻田散鐵之面積率未滿忉％，伸展 ❹凸緣性劣化。又’若再加熱溫度超過_t:或婦時間超過 600s則冷辦所生成之未變態輯田鐵變態為波來鐵或變 _，最賊吨鐵㈣留沃斯喊之㈣率合計未滿 3% TS E1平衡劣化’ YR增加。從而，回火時之再加熱必需 依於350〜600Ϊ之溫度區域保持卜_s之條件進行。 、其他製造方法之條件’並無特別限定，較佳係依以下條件 谁杆。 為了防止她發生微騎，較佳係依連_造法進行製 造’可藉由造塊法、薄鋼_造法予以製造。對鋼㈣行载 ^時，可將舰先暫時冷卻至室溫，其後進行再加熱而進行 …軋’亦可不將鋼料卻至室溫叫人加熱爐中進行孰札。 或者亦可賴於進行了 保熱後立即進行熱札的省能製 對娜進行加熱時，為了防止使碳化物溶解、或壓⑽ 之增加，較佳係加熱至⑽代以上。又，為 損失一一 ’較佳係將鋼述之加熱溫度設: 097140611 17 200927990 1300°C 以下。 對鋼述進行熱軋時，由確保麼乳溫度之觀點而言，亦可將 粗軋後之粗棒進行加熱。又，可應用將粗棒彼此接合，連續 • 地進行精軋之所謂連續壓軋製程。為了防止使冷軋·回火後 • 之加工性降低、或異向性增加之原因的帶狀組織形成，精軋 車父佳係依An變態點以上之完工溫度進行。又，為了減低壓 軋負重或形狀•材質之均勻化，較佳係於精軋之全部路徑或 ❹一部分路徑進行摩擦係數為0. 1〇〜〇. 25之潤滑壓軋。 熱軋後之鋼板係由溫度控制或防止脫碳的觀點而言，較佳 係依450〜700°C之捲取溫度進行捲取。 捲取後之鋼板係藉酸洗等去除銹皮後，較佳係依壓下率 40%以上進行冷軋，依上述條件進行回火，實施熔融鍍鋅。 熔融鍍鋅係在不將鑛鋅進行合金化時，將鋼板浸潰於含 A1量0.12〜0. 22%之440〜50(TC鍍浴中，或在將鍍鋅進行合 Φ 金化時’將鋼板浸潰於含A1量〇. 〇8~0. 18%之440〜500。(^贫 浴中，其後，藉氣體拭焊（Gas Wiping)等調整鍍敷附著量而 進行。在將鍍鋅進行合金化時，其後，再以450〜6〇〇它施行 1〜30秒之合金化處理。 對於經施行溶融鑛辞後之鋼板、或進一步施行了鑛辞之人 金化處理後的鋼板，可依形狀矯正或調整表面粗度等為目的 而進行調質壓軋。另外，亦可實施樹脂或油脂塗佈等之各種 塗裝處理。 097140611 18 200927990 4)製造條件260%, you can't get the second phase of TSx ‘built to high intensity. The area ratio of the scattered iron in 1 field is 10% or more. The area ratio of the tempered granulated iron is set to Tian Tie's superior stretch flangeability to the unfavorable flangeability, and it is effective. If this effect is obtained, it is necessary to make the tempering. However, if the tempering plant is surveyed 10~60% of 杂 〇 〇 〇 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 250 The presence of the second phase with the residual Worthfield iron and the tempered granules is effective for improving the impact resistance. In particular, AE/TS20.063 can be achieved by making the average crystal grain size of the second phase 3/m or less. Therefore, the average crystal grain size of the second phase containing the granulated iron and the residual Worth iron and the tempered granulated iron is preferably 3 " m or less. It is also the second phase of the 麻 散 散 、 、 残留 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻The area ratio of the Wostian Iron, the tempered Ma Tian Iron, or the average crystal grain control of the second phase achieves the object of the present invention. Further, from the viewpoint of the stretched flange property, the area ratio of the Borne iron is preferably 3% or less. The area ratio of 'fertilizer iron, 麻田散铁, residual Worth iron, tempered 麻田散铁 refers to the proportion of each phase in the observed area, which can be obtained by the plate thickness profile of the steel plate After the grinding, the rot is cooked with 3% nitric acid etch solution (Nital), and the SEM (scanning electron microscope) is used to observe the thickness of 1/4 of the thickness of 1000~3000 097140611 14 200927990, and the commercially available image processing software is used. And ask for it. In addition, the total area of the second phase containing the granulated iron, the residual Worth iron, and the tempered granulated iron is divided by the total number of the second phase, and the uneven area of each second phase is determined. The square root is used as the average crystal grain of the second phase. (3) Manufacturing conditions 1 ❹ 高 The high-strength molten zinc-zinc steel sheet of the present invention can be produced by the following method: for example, the steel having the above-mentioned pure steel is subjected to reduction and cold rolling to form a cold-rolled steel sheet. After heating the cold-rolled steel sheet to a temperature range of 75q to 9th order and maintaining it for 1Gs or more, it is cooled from the 75th generation by 1 (r/s or more of the cold part speed to (Ms point is heated to the temperature range of _ΐ and After the tempering is carried out to maintain the conditions of the coffee s, the molten zinc is applied. The heating condition at the time of tempering: at 75 () to 95 (the temperature region of rc is maintained above the heating temperature at the time of tempering is less than 75 ( When the rc or the holding time is not full, the formation of the Voss is insufficient, and the second phase such as the Ma Tian loose iron cannot be covered by the cooling. Further, if the heating temperature exceeds 95 Qt, the Worthite iron is coarsened. 'The grain of iron is suppressed, and the grain iron of the above area cannot be obtained. Therefore, the heating system at the time of tempering is set to maintain a temperature of more than 1 〇s in the temperature range of 75 M5 〇f. No special rules, even if it is held in 600s, its effect is fresh, resulting in increased costs. Add, so it is better to set the holding time to less than 600s. Cooling conditions during tempering: average cooling rate of 耽/s or more from the 75th generation 097140611 15 200927990 degree m point meter MMs point reading) After heating, must be 7503⁄4 is cooled by l〇t/s, but if the average cooling catch is not full] 〇t/ the average ^ but the speed into the iron, can not get the required amount of tempering Ma Tian _S' then generate a large number of Bo Laitian Iron. The upper limit of the cooling rate is not (9) loose iron and residual Woss, it is difficult to control the cooling (MS point - (10). c) ^ 'But because the shape of the steel plate is unstable, the temperature is stopped, so it is better to set it to 2 〇〇t/s is controlled by the cooling degree of 3 points. The cold is more than the stop temperature...the...the ferritic and galvanized, the alloying of the plating phase Vostian Iron, Hui ^ is the most important condition of the invention - n iron, and the amount of iron and untransformed compilation, followed by;; 7 when the mosquito Ma Tian scattered for tempering Ma Tian San _, |_ ”,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,,, A, the flangeability, YR. If it is cold, to pay the energy point -100. 0, then the Ma Tian loose iron becomes green;? The untransformed Worth Iron is not enough metamorphosis, the area ratio is more than 10〇/ ^ The temperature of the loose iron and the residual Worthite iron is not full of scattered iron, and it has not changed. _ The iron of the Tiantian is almost metamorphosed into the arada, and the amount of the iron of the Tianstian is reduced. The total area ratio of the Tiantie is not (4) The tempering balance is degraded and the YR is increased. The cooling rate is determined by the average condition of 75 mrc/s or more. orc) ~ (Ms point ~ 200. 温度 temperature zone 097140611 16 200927990 Reheating condition during tempering: at 35 〇~6〇 (The temperature zone of rc is kept at 1~600s and cooled to (10) point at an average cooling rate of 10 C/s or more. c point -2〇〇. After the temperature zone of the 〇, by reheating in the temperature zone of the lake ~, it is possible to temper the red iron in the kenaf field and temper it into a tempered granulated iron with an area ratio of 10~60%. Excellent stretch flangeability can be maintained and high strength can be achieved. If the reheating temperature is less than 350 °C or /, the temple is less than Is', the area ratio of the tempered granulated iron is less than 忉%, and the flangeability of the stretch 劣化 is deteriorated. Also, if the reheating temperature exceeds _t: or the woman's time exceeds 600s, the untransformed field iron produced by the cold office is transformed into a wave of iron or a change _, the most thief tons of iron (four) Revos shouts (four) rate is not full 3% TS E1 balance degradation 'YR increases. Therefore, the reheating at the time of tempering must be carried out in accordance with the condition that the temperature region of 350 to 600 Torr is maintained. The conditions of other manufacturing methods are not particularly limited, and it is preferred to be based on the following conditions. In order to prevent her from riding slightly, it is preferable to manufacture it by the method of making a block and thin steel. When the steel (4) is loaded, the ship can be temporarily cooled to room temperature, and then reheated to carry out the rolling, or the steel material can be cooled to room temperature in a heating furnace. Alternatively, it may be heated to (10) or more in order to prevent the carbide from being dissolved or the pressure (10) from being increased when the heat treatment is performed immediately after the heat retention. Also, for the loss one by one, the heating temperature of the steel is preferably set to 097140611 17 200927990 1300 ° C or less. When hot rolling is performed on the steel, the thick rod after the rough rolling may be heated from the viewpoint of ensuring the temperature of the milk. Further, a so-called continuous rolling rolling process in which the thick rods are joined to each other and the finish rolling is continuously performed can be applied. In order to prevent the formation of a band structure which causes a decrease in workability after cold rolling and tempering, or an increase in anisotropy, the finish rolling mill is carried out at a temperature higher than the completion temperature of the An abnormal point. Further, in order to reduce the load of the low-pressure rolling load or the uniformity of the shape and the material, it is preferable to carry out the lubrication of the entire path of the finish rolling or a part of the path of the friction coefficient of 0. 1〇~〇. The steel sheet after hot rolling is preferably wound up at a coiling temperature of 450 to 700 ° C from the viewpoint of temperature control or prevention of decarburization. After the coiled steel sheet is removed by pickling or the like, it is preferably cold-rolled at a reduction ratio of 40% or more, and tempered under the above conditions to carry out hot-dip galvanizing. The hot-dip galvanizing is performed by immersing the steel sheet in a 440 to 50 (TC plating bath containing A1 amount of 0.12 to 0.22%) or when galvanizing is performed. The steel plate is immersed in the amount of A1. 〇8~0. 18% of 440~500. (^ In the lean bath, thereafter, the amount of plating adhesion is adjusted by Gas Wiping or the like. When galvanizing is alloyed, it is then subjected to alloying treatment for 1 to 30 seconds at 450 to 6 Torr. After the metallurgical treatment of the steel plate after the execution of the molten ore, or the further implementation of the mineralization The steel sheet may be subjected to temper rolling in order to correct the shape or adjust the surface roughness, etc. Further, various coating treatments such as resin or grease coating may be applied. 097140611 18 200927990 4) Manufacturing condition 2

本發明之高強度熔融鍍辞鋼板，可藉由下述方法予以製 造··將具有上述成分組成之鋼坯施行熱軋、冷軋而作成冷軋 鋼板，以對上述冷軋鋼板，於500°C〜Ac〗變態點之溫度區域 依10°C/s以上之平均升溫速度進行升溫，加熱至Aci變態 點〜（Acs變態點+30。〇之溫度區域並保持1〇s以上後，以1〇 C /s以上之平均冷卻速度冷卻至（Ms點-1 〇(Tc )〜（MS點-200 C)之溫度區域，再加熱至350〜600t之溫度區域並保持 1〜600s之條件而實施回火後，施行熔融鍍鋅。 回火時之加熱條件：於5〇〇°C〜AC1變態點之溫度區域依1〇 °C/s以上之平均升溫速度進行升溫 、回火時之升溫速度係用於使含有麻田散鐵、殘留沃斯田 鐵、回火麻田散鐵之第二相之平均結晶粒徑變得細微的重要 條件。於具有本發明之成分組成之鋼中，係藉由H v ==抑制再結晶’但若於變態點之溫度 上之平均升溫速度進行升溫，則幾乎不發 ΐ 之Ae,變態如上之溫度區域。因 L微=鼓未再Μ輯明鶴，而生成 細微之沃斯田鐵，故冷卻成 徑成為平均結晶粒 另一方面，於咖。⑽變態點之溫;==衝擊特性。 未滿時，在升Μ之域之=升溫速度 叫0C〜Aci變態點之溫度 097140611 200927990 區域發生再結晶’再結晶肥粒鐵騎隸度之粒成長後而進 行沃斯田鐵變態，故未達到沃斯田鐵之細微化，無法使第二 相之平均結晶粒徑成為3Am以下。因此，必須於5〇〇它〜心^ 變態點之溫度區域依1(rc/s以上、較佳2()<t/s以上之平均 升溫速度進行升溫。 回火時之加熱條件.於Aei變態點〜(Αα變態點畑。◦)之溫 度區域保持10s以上 ❹ ❹ :回火時之加熱溫度為未滿A。變態點或保持時間未滿 10s時’不發生沃斯田鐵之生成或不足，於其後之冷卻無法 ” 77量之麻田散鐵等第二相。又’若加熱溫度超過（仏 變態點+3G°C) ’則沃斯田鐵之粒成長顯著，無法到達沃斯田 鐵之細微化。又，由於沃斯田鐵粒之粒成長，抑制冷卻時之 肥生成’而無法得到面積率2_上之肥粒鐵。從而， 二1=熱必需依於Aci變態點〜(Ac3變態點載)之溫 以上?條件進行。又，保持時間係由沃斯田 制或能1成本之觀點而言，較佳設為300s以 下0 條件:自加熱溫度以1〜上之平均冷卻 點_2(H)°C)之溫度區域 絲;2，自加熱溫相1(rc/s以上之平均冷卻速度 " 但右平均冷卻速度未滿1(rc/s， 來鐵’無法得到所需量之回火麻田散鐵、麻田散 097140611 20 200927990 斯田鐵。冷卻速度之上輯並鱗職定，由於 惡化、難以將冷卻控制在n10(rc)~(Msi^2〇 ^ 卻停止溫度區域，故較佳係設為2〇〇〇c/s以下。 之冷The high-strength hot-dip steel plate of the present invention can be produced by the following method: The steel slab having the above-described composition is hot-rolled and cold-rolled to form a cold-rolled steel sheet at 500 ° C for the cold-rolled steel sheet. ~Ac〗 The temperature region of the metamorphic point is heated at an average heating rate of 10 ° C / s or higher, and heated to the Aci metamorphic point ~ (Acs metamorphic point + 30. After the temperature region of 〇 and maintained for 1 〇 s or more, 1 〇 The average cooling rate above C / s is cooled to a temperature range of (Ms point -1 〇 (Tc) ~ (MS point - 200 C), and then heated to a temperature range of 350 to 600 t and maintained for 1 to 600 s. After the fire, hot-dip galvanizing is carried out. Heating conditions during tempering: temperature rise at a temperature rise rate of 5 ° ° C to AC 1 at an average temperature rise rate of 1 ° C / s or more, and a temperature rise rate at the time of tempering An important condition for making the average crystal grain size of the second phase containing the granulated iron, the residual Worth iron, and the tempered granulated iron into a fine. In the steel having the composition of the present invention, it is by H v == inhibit recrystallization 'but the average heating rate at the temperature of the metamorphic point When the temperature is raised, the Ae is almost untwisted, and the temperature region is as described above. Since the L micro = drum does not reproduce the crane, the fine Worth iron is generated, so that the cooling becomes the average crystal grain. (10) Temperature of the metamorphic point; == Impact characteristics. When not full, in the domain of the ascending = = temperature rise rate is 0C~Aci metamorphic point temperature 097140611 200927990 area recrystallization 'recrystallized fat iron riding degree After the grain grows, the Worthite iron metamorphosis is carried out, so that the fineness of the Worthite iron is not achieved, and the average crystal grain size of the second phase cannot be made 3 or less. Therefore, it must be at 5 〜 The temperature region is increased by an average temperature increase rate of 1 (rc/s or more, preferably 2 () < t/s or more. Heating conditions during tempering. Temperature at Aei metamorphic point ~ (Αα metamorphic point 畑.◦) The area is kept for more than 10s ❹ ❹ : The heating temperature during tempering is less than A. When the metamorphic point or holding time is less than 10s, 'the formation or deficiency of Worthite iron does not occur, and the cooling cannot be performed afterwards.” Second phase such as loose iron. Also 'If the heating temperature exceeds (仏 metamorphic point +3G °C ) 'When the Worthite iron grain grows significantly, it can't reach the fineness of the Worthite iron. Also, because the grain growth of the Worthfield iron grain inhibits the formation of fertilizer during cooling', the area ratio cannot be obtained. Fertilizer iron. Thus, the temperature of the two 1 = heat must be based on the temperature above the Aci metamorphosis point ~ (Ac3 metamorphic point load). Also, the retention time is from the viewpoint of the cost of the Worth or the cost. Set to less than 300s. 0 Condition: Self-heating temperature is 1~ upper average cooling point _2 (H) °C) temperature zone wire; 2, self-heating temperature phase 1 (average cooling rate above rc/s) The average average cooling rate is less than 1 (rc/s, and the iron can't get the required amount of tempered Ma Tian loose iron, Ma Tian scattered 097140611 20 200927990 sita iron. The cooling rate is set to be equal to the scale, and it is difficult to control the cooling to n10(rc)~(Msi^2〇^ but the temperature range is stopped, so it is preferably set to 2〇〇〇c/s or less. cold

冷卻之停止溫度係控制其後之再加熱、炫融鍍鋅、鍍敷相 之合金化處理時所生成之麻田散鐵、殘料斯田鐵、回火才 田散鐵之量，而為本發明最重要的條件之一。亦即，冷、二 止時決定麻田散鐵與未變態沃斯田鐵之量，於其後部停 中，麻田散鐵成為回火麻田散鐵，未變態沃斯田鐵=理 散鐵或殘留沃斯田鐵’左右著鋼強度、TS，平衡伸 :=冷二T溫度超過(…rc)，則麻： 變態不足’未變態沃斯田鐵之量變多’最终麻田散鐵與殘留 沃斯田鐵之面積率合計超過1Q%，伸展凸緣性降低。另一方 面’冷卻之停止溫度未滿（Ms點_細。〇時，_田鐵The cooling stop temperature is the amount of the granulated iron, the residual material, and the tempered iron produced by the reheating, the glazing, and the alloying treatment of the plating phase. One of the most important conditions. That is to say, when the cold and the second stop, the amount of the granulated iron and the untransformed Worthite iron was decided, and it was stopped at the back. The granulated iron became the tempered granulated iron, and the untransformed Worth iron = the iron or the residue Vostian Iron's left and right steel strength, TS, balance extension: = cold two T temperature exceeds (...rc), then hemp: abnormality is not enough 'unchanged Worthite iron amount becomes more 'final Ma Tian loose iron and residual Voss The area ratio of Tian Tiezhi is more than 1Q%, and the stretch flangeability is reduced. On the other hand, the cooling stop temperature is not full (Ms point _ fine. When 〇, _ Tian Tie

變態為麻錢鐵，未變該斯喊之㈣少，最終麻田散鐵 與殘留沃斯田鐵之面積率合計未滿3%，而TS-E1平衡劣化。 從而’回火時之冷卻必須依自加熱溫度以财/s以上之平 均冷卻速度冷卻至（Ms點-咖以〜⑽點_⑽。c)之溫度區 域的條件進行。 回火叙再加熱條件：於35㈣_之溫度區域簡Ls 以10 C/s以上之平均冷卻速度冷卻至.點一刚。㈡〜⑽ 點-2〇(TC)之溫度區域後，藉由進行於麵。c之溫度區 域保持Is以上之再加熱，可對冷卻時所生成之細散鐵進 097140611 21 200927990 行回火，生成面積率10〜60%之回火麻田散鐵，可維持優異 之伸展凸緣性並達成高強度化。若再加熱溫度未滿3 5 〇 t或 保持時間未滿則回火麻田散鐵之面積率未滿1〇%，伸展 凸緣性劣化。又，若再加熱溫度超過600Ϊ或保持時間超過 • 600s，則冷卻時所生成之未變態沃斯田鐵變態為波來鐵或變 韌鐵，最終麻田散鐵與殘留沃斯田鐵之面積率合計未滿 3%，TS-E1平衡劣化。從而，回火時之再加熱必需依於 〇 350~60(TC之溫度區域保持卜600s之條件進行。 其他製造方法之條件，並無特別限定，較佳係依以下條件 進行。 為了防土鋼坯發生微偏析，較佳係依連續鑄造法進行製 造，可藉由造塊法、薄鋼坯鑄造法予以製造。對鋼坯進行熱 軋時，可將鋼坯先暫時冷卻至室溫，其後進行再加熱而進行 熱軋，亦可不將鋼坯冷卻至室溫而裝入加熱爐中進行熱軋。 ❹或者亦可應用於進行了稍微保熱後立即進行熱軋的省能製 程。對鋼述進行加熱時，為了防止使碳化物溶解、或壓軋負 重之增加，較佳係加熱至110(rc以上。又，為了防止銹皮 損失之增加，較佳係將鋼坯之加熱溫度設為13〇〇它以下。 對鋼坯進行熱軋時，由確保壓軋溫度之觀點而言，亦可將 粗軋後之粗棒進行加熱。又，可應用將粗棒彼此接合，連續 地進行精軋之所謂連續壓軋製程。為了防止使冷軋·回火後 之加工性降低、或異向性增加之原因的帶狀組織形成，精軋 097140611 22 200927990 較佳係依An變態點以上之完卫溫度進行。又，為了減低壓 軋負重或形狀•材質之均勻化，較佳係於精軋之全部路徑或 一部分路徑進行摩擦係數為〇. 10〜0. 25之潤滑壓乳。 - 熱軋後之鋼板係由溫度控制或防止脫碳的觀點而言，較佳 • 係依450〜700°C之捲取溫度進行捲取。 捲取後之鋼板係藉酸洗等去除銹皮後，較佳係依壓下率 40%以上進行冷軋，依上述條件進行回火，實施熔融鍍鋅。 ❹ 熔融鍍辞係在不將鍍鋅進行合金化時，將鋼板浸潰於含 A1量0.12〜0.22%之440〜50(TC鑛浴中，或在將錢鋅進行合 金化時’將鋼板浸潰於含A1量〇. 〇8〜0. 18%之440〜50(TC鍍 浴中，其後，错耽體拭焊等調整鍵敷附著量而進行。在將鑛 辞進行合金化時，其後’再以450〜600X：施行1〜30秒之合 金化處理。 對於經施行溶融鑛辞後之鋼板、或進一步施行了鑛辞之人 ❹ 金化處理後的鋼板，可依形狀矯正或調整表面粗度等為目的 而進行調質壓軋。另外，亦可實施樹脂或油脂塗佈等之各種 塗裝處理。 (實施例） (實施例1) 將表1所示成分組成的鋼A〜S藉轉爐進行熔製，以連續製 造法作成鋼坯後’依完工溫度900 °C進行熱軋為板厚 3. 0mm，於壓軋後以10°C/s之冷卻速度進行冷卻，依6〇〇。〇 097140611 23 200927990 之捲取溫度予以捲取。其次，酸洗後，冷軋為板厚L 2mm， 藉連續炼融鐘鋅產線，依表2、3所示之回火條件進行回火 後，浸潰於460°C之鍍浴中，形成附著量35〜45g/m2之鑛敷， - 並於520°C進行合金化處理，依冷卻速度/秒進行冷 • 卻，製作鍍敷鋼板卜44。又，如表2、3所示，一部分鍍敷 鋼板未進行合金化處理。然後，針對所得之鍍敷鋼板，依上 述方法測定肥粒鐵、麻田散鐵、殘留沃斯田鐵、回火麻田散 ❹鐵之面積率。又’於壓軋方向之直角方向上採取jIS 5號拉 伸試驗片，根據皿2241進行拉伸試驗。進一步採取15〇咖 :15〇咖之試驗片’根據肌T1001(鐵連規格）進行3次擴孔 試驗而求取平均之擴孔率λ⑻，評價伸展凸緣性。 結果示於惠 乂 Γ 、4、5。可知本發明例之鍍敷鋼板係均TSxEl $ _a·%而TS—E1平衡高’擴孔率Ay〇%而伸展凸緣 性優越，伙<75%而YR低。 ❹ 097140611 24 200927990 $The metamorphosis is numb iron, and the screaming (four) is not changed. In the end, the area ratio of the granulated iron and the residual Worth iron is less than 3%, and the balance of TS-E1 is degraded. Therefore, the cooling at the time of tempering must be carried out under the condition of the temperature range of (Ms point - coffee at ~(10) point _(10).c) from the heating temperature at an average cooling rate of more than s/s. The tempering reheating condition is: in the temperature range of 35 (four) _, the Ls is cooled to an average cooling rate of 10 C/s or more. (b) After the temperature zone of ~(10) point -2〇(TC), it is carried out by the surface. The temperature region of c is maintained at a reheating of Is or more, and the fine iron generated during cooling can be tempered into 097140611 21 200927990 to form a tempered granulated iron with an area ratio of 10 to 60%, which can maintain an excellent stretch flange. Sexuality and high intensity. If the reheating temperature is less than 3 5 〇 t or the holding time is not full, the area ratio of the tempered granulated iron is less than 1%, and the stretch flangeability is deteriorated. Moreover, if the reheating temperature exceeds 600 Ϊ or the holding time exceeds 600 s, the untransformed Worth iron formed during cooling is metamorphosed into bun or iron, and finally the area ratio of the granulated iron and the residual Worth iron When the total is less than 3%, the TS-E1 balance deteriorates. Therefore, the reheating at the time of tempering must be carried out in accordance with the conditions of 〇350 to 60 (the temperature region of TC is maintained for 600 s. The conditions of other manufacturing methods are not particularly limited, and are preferably carried out under the following conditions. Microsegregation occurs, preferably by continuous casting, and can be produced by agglomeration method or thin billet casting method. When hot rolling a billet, the billet can be temporarily cooled to room temperature and then reheated. In the case of hot rolling, the slab may be placed in a heating furnace without being cooled to room temperature for hot rolling. ❹ Or may be applied to an energy-saving process in which hot rolling is performed immediately after heat retention. In order to prevent the carbide from being dissolved or the weight of the rolling load is increased, it is preferably heated to 110 (rc or more. Further, in order to prevent an increase in the loss of the scale, it is preferred to set the heating temperature of the steel slab to 13 〇〇 or less. When the slab is hot-rolled, the thick rod after the rough rolling may be heated from the viewpoint of ensuring the nip temperature. Further, the so-called continuous pulverization in which the coarse rods are joined to each other and the finish rolling is continuously performed may be applied. In order to prevent the formation of a band structure which causes a decrease in workability after cold rolling and tempering or an increase in anisotropy, the finish rolling of 097140611 22 200927990 is preferably carried out at a temperature above the deformation point of the An abnormal point. In order to reduce the load of the low-pressure rolling load or the uniformity of the material and the material, it is preferable to carry out the lubrication of the whole or a part of the path of the finishing rolling with a coefficient of friction of 〇. 10~0. 25 - the temperature of the steel plate after hot rolling is temperature From the viewpoint of controlling or preventing decarburization, it is preferable to perform coiling at a coiling temperature of 450 to 700 ° C. After the coiling, the steel sheet is removed by pickling or the like, and the reduction ratio is preferably 40% or more of the cold rolling is performed, and tempering is performed according to the above conditions, and hot-dip galvanizing is performed. 熔融 The molten plating is performed by immersing the steel sheet in a 440 to 50-containing A1 amount of 0.12 to 0.22% when the galvanization is not alloyed. (In the TC mineral bath, or when alloying the zinc and zinc), the steel plate is immersed in the amount of A1. 〇8~0. 18% of 440~50 (TC plating bath, after which, the wrong body wipe Welding is performed by adjusting the amount of bonding of the bond. When the mineral is alloyed, it is then 450~600X: The alloying treatment is carried out for 1 to 30 seconds. For the purpose of correcting the shape or adjusting the surface roughness, the steel sheet after the molten ore is applied or the steel sheet which has been further subjected to the mineralization is used. Quenching and temper rolling, and various coating treatments such as resin or grease coating may be applied. (Examples) (Example 1) Steels A to S having the composition shown in Table 1 were melted by a converter to After the continuous production method is made into a steel slab, it is hot-rolled at a temperature of 900 ° C to a thickness of 3.0 mm, and is cooled at a cooling rate of 10 ° C/s after rolling, according to 〇〇. 〇 097140611 23 200927990 Take the temperature and take it up. Secondly, after pickling, the cold rolling is a thickness of L 2 mm, and after tempering according to the tempering conditions shown in Tables 2 and 3, the steel is continuously tempered, and then immersed in a plating bath at 460 ° C. An ore deposit of 35 to 45 g/m2 was formed, and alloyed at 520 ° C, and cooled at a cooling rate/second to prepare a plated steel sheet 44. Further, as shown in Tables 2 and 3, some of the plated steel sheets were not alloyed. Then, with respect to the obtained plated steel sheet, the area ratio of the ferrite-grained iron, the granulated iron, the residual Worthite iron, and the tempered granules was determined by the above method. Further, a jIS No. 5 tensile test piece was taken in the direction perpendicular to the rolling direction, and a tensile test was carried out in accordance with the dish 2241. Further, the test piece of 15 〇 : 〇 〇 〇 〇 〇 〇 ’ ’ ’ ’ ’ ’ ’ ’ ’ 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌 肌The results are shown in Hui 乂 4, 4, 5. It can be seen that the plated steel sheets of the examples of the present invention have a TSxEl $ _a·% and a high balance of TS-E1 and a hole expansion ratio of Ay 〇 %, and the stretch flangeability is excellent, and the ratio is < 75% and the YR is low. 097 097140611 24 200927990 $

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ZI 01 01 91 60 000ZI 01 01 91 60 000

ZO 寸0ZO inch 0

SI 80 壤SI 80 soil

V 3 0V 3 0

H 1-3 0 cu s 50 寸 U60 200927990H 1-3 0 cu s 50 inch U60 200927990

備註 發明例 比較例 比較例 發明例 比較例 比較例1 發明例 比較例j 比較例 I發明例1 比較例 I比較例1 發明例 1比較例j 1比較例1 I比較例j 發明例 比較例 1比較例1 1比較例1 發明例 比較例 合金化處理 杯 •VF 杯 磔 墀 磡 杯 Ms點 (0〇 CO 1〇 CO m 呀 οα CO oo CO 00 Cvl CO ιΟ CO CNI CO cn> L〇 CO CO I·1 Η CO <M s (N1 C<l <NI 05 οα <NI oo 呀 οα <=) <>α οα 〇〇 οα oo (Nl <ΝΙ a> 03 回火條件 再加熱 保持時間 (S) s S § L〇 in 寸 L〇 寸 s s s 写 s § g <=> ο ο 05 ο σ> 再加熱溫度 (°C) 〇 呀 430 o CO o 导 寸 o m o LTD 寸 o 兮 450 s 寸 c? g CO s CO o ο 〇 〇 s 呀 ο ο g ο s 冷卻 到達溫度 CC) 〇 CD οα 1 1 o c— o L〇 s T-H o CM l—H o oo g Cv3 g CD CO <=> CO ◦ ο 1· < 〇 ο ο CO ο m ο 冷卻速度 (°C/s) S s s s § LTD 茭 o 卜 s o <〇 c? 〇o § s § § § § s ο ο G> o 加熱 保持時間 (S) ο CO § g o <3^ L〇| § § § o 0¾ o LO o CO § L〇 s L〇 L〇 卜 ο <ΝΙ <ΝΙ 03 CD 呀 (Νϊ ο CO § 加熱溫度 (到達溫度） (°C) CO 〇〇 ο CD 00 780 o 00 s o 00 oo s oo § oo o oo 780 o oo cr> L〇 oo o uO oo o CO oo 〇> ΙΟ oo ο s 〇〇 ο s ο s oo s oo CO c t3 U Lh c 鍍敷鋼板 No. οα CO L〇 CO 卜 oo 03 o r-H oa CO L〇 CO p- H 卜 〇〇 03 OJ CO 93 U90--0 200927990 (s) 備註 發明例 比較例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 比較例 比較例 比較例 合金化處理 杯 杯 杯 碟 杯 碟 碟 杷 杯 +F Ms點 rc) CO CO CO CO ο οο CO § CO ο οο CO 03 03 CO 〇〇 CO 00 寸 CO 03 寸 CO OJ 却 CO 寸 CO CO OO 宕 ΟΟ 05 OO CO CT5 〇〇 CO CO CO S3 CO CO —1 回火條件 再加熱 保持時間 (S) 另 另 ΙΛ ΙΟ S 〇 ο § § s E § S ο LO 1—ί § 再加熱溫度 ΓΟ ο s CO ο s ο s ο Ο 写 S 1〇 ο ΙΛ m ο 导 ο 导 ο 写 〇 〇 〇 〇 m 〇 1Λ 寸 〇 〇 ο 〇 〇 冷卻 到達溫度 CC) g g <〇 03 ο ΙΛ 03 ο 另 § 〇 S ο CO οα ο ο CO ο οο 〇 §5 S S 〇 03 03 〇 CO 〇 § F-H 冷卻速度 (°C/s) § § s r-H Ο U0 s § § 〇 ο ο ο LO ο LO CD ΙΟ S S S 1000 1000 § § 'SE τ—Η <〇 <N1 s ?—1 LO LO 〇 〇 <NI ο ο οα s r-H G § § g m 寸 LTD § § LO 加熱溫度 (到達溫 度） CC) <ζ> οο G> 寸 oo 1000 Ο CO οο o CO oo ο § <3 TO ο LO ο LO ο οο 〇> oo CD oo OO § 〇〇 ο §s ο § ο § 〇 C? 〇 § OO 〇 03 00 >—i 2: C P L, οι 〇£： GQI 鍍敷 鋼板 No. c^a §3 τ—< CO LO CO OO CO 05 CO $Remarks Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example 1 Inventive Example Comparative Example j Comparative Example I Inventive Example 1 Comparative Example 1 Comparative Example 1 Inventive Example 1 Comparative Example j 1 Comparative Example 1 I Comparative Example j Inventive Example Comparative Example 1 Comparative Example 1 1 Comparative Example 1 Inventive Example Comparative Example Alloying Treatment Cup•VF Cup Cup Ms Point (0〇CO 1〇CO m 呀οα CO oo CO 00 Cvl CO ιΟ CO CNI CO cn> L〇CO CO I·1 Η CO <M s (N1 C<l <NI 05 οα <NI oo 呀οα <=) <>α οα 〇〇οα oo (Nl <ΝΙ a> 03 tempering condition Reheating hold time (S) s S § L〇in inch L〇 inch sss write s § g <=> ο ο 05 ο σ> Reheating temperature (°C) 〇 430 o CO o Guide omo LTD寸o 兮450 s inch c? g CO s CO o ο 〇〇s 呀ο ο g ο s cooling arrival temperature CC) 〇CD οα 1 1 oc- o L〇s TH o CM l-H o oo g Cv3 g CD CO <=> CO ◦ ο 1· < 〇ο ο CO ο m ο Cooling rate (°C/s) S sss § LTD 茭o 卜so <〇c? 〇o § s § § § § s ο ο G> o Heat retention time (S) ο CO § go <3^ L〇| § § § o 03⁄4 o LO o CO § L〇s L〇L〇卜ο <ΝΙ <ΝΙ 03 CD 呀( Νϊ ο CO § Heating temperature (arrival temperature) (°C) CO 〇〇ο CD 00 780 o 00 so 00 oo s oo § oo o oo 780 o oo cr> L〇oo o uO oo o CO oo 〇> ΙΟ Oo ο s 〇〇ο s ο s oo s oo CO c t3 U Lh c Plated steel plate No. οα CO L〇CO oo 03 o rH oa CO L〇CO p- H 〇〇 03 OJ CO 93 U90- -0 200927990 (s) Remarks Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Comparative Example Comparative Example Example alloying cups cups cups cups and saucers cups + F Ms points rc) CO CO CO CO ο οο CO § CO ο οο CO 03 03 CO 〇〇CO 00 inch CO 03 inch CO OJ but CO inch CO CO OO宕ΟΟ 05 OO CO CT5 〇〇CO CO CO S3 CO CO —1 Tempering condition Reheat retention time (S) Another Ι ΙΟ S 〇ο § § s E § S ο LO 1—ί § Reheating temperature ο ο s CO ο s ο s ο Ο Write S 1〇ο ΙΛ m ο Guide ο Guide ο write 〇〇〇〇m 〇1Λ inch 〇〇ο 〇〇Cooling to temperature CC) gg <〇03 ο ΙΛ 03 ο §S ο CO οα ο ο CO ο οο 〇§5 SS 〇03 03 〇CO 〇§ FH Cooling speed (°C/s § § s rH Ο U0 s § § 〇ο ο ο LO ο LO CD ΙΟ SSS 1000 1000 § § 'SE τ—Η <〇<N1 s ?-1 LO LO 〇〇<NI ο ο οα s rH G § § gm inch LTD § § LO heating temperature (arrival temperature) CC) <ζ> οο G> inch oo 1000 Ο CO οο o CO oo ο § <3 TO ο LO ο LO ο οο 〇> oo CD oo OO § 〇〇ο §s ο § ο § 〇C? 〇§ OO 〇03 00 >—i 2: CPL, οι 〇£: GQI Plated Steel Plate No. c^a §3 τ—< CO LO CO OO CO 05 CO $

LI U9§U60 200927990LI U9§U60 200927990

Q S 備註 發明例 比較例 比較例 發明例 比較例 比較例 發明例 丨比較例 比較例 發明例 比較例 比較例 發明例 比較例 比較例 比較例 發明例 比較例 比較例 比較例 發明例 比較例 r< 0 s § LO CO § OO CO LO oo 03 拉伸特性值 TSxEl (MPa · %) 21440 15125 1T732 21627 16060 18630 20559 15521 | 17820 19170 1 15600 15442 20910 21114 14784 17650 19734 19470 16400 19110 21952 17450 〇〇 LO OO 00 CO CO CD 00 OO c— CO 寸 OO § OO 卜 05 CD LO CO CO oo CO ιο oo s CO C^- sg 03 CO LO oa CO CM S 03 CS1 CO 03 二 OO 〇〇 LO m m 03 CO C^J 03 OCJ s 口 <>3 CO in oa TS (MPa) o CO S CO C<l OO CO OO o CO 〇> 53 05 03 CO CD o cn> 05 1065 1040 1103 5¾ CO 03 〇0 却 o CO o oo LO 00 LTD OO OO o oa oo ο σ> CO oo CO oo 05 CO YS (MPa) <x> oo CO s LO oo LO CO LO LO oo <NJ CO 03 CO CD LO r—H S 卜 <>a 〇〇 〇〇 寸 CO oo c— OO g LO oo Lrt ΙΛ oo CD CO 0¾ LT> 05 CO CO 呀 ΙΛ 00 lO 微組織t 其他 1 1 CQ (X. 1 Oh 1 1 1 CQ 1 1 CU 1 1 1 1 CQ 1 1 回火M 面積率 ⑻ CO Cs3 c^- T—· OO LOl <NI 寸 r-H O〇 (Nl C<l <NI CO CO CO CNI LO CO1 CO οα C<I CvJ σο CO CO 卜 寸 (Nl m殘留γ 面積率 (¾) 寸 <NI r—< ID 寸 卜 03 05 CO eg CO CO T—< 1—«1 c〇 r-H 卜 LO I F 面積率 (%) § C 0¾ iM OO C^3 in oo 〇 c^- CO OO 05 in CO CO r—H CO 5S C-- O S m CO c^a 00 鍍敷 鋼板 No. 1—^ oa CO m CO c— OO 05 ο r-H — CO — CO t—1 L〇 CO c— OO 03 C<l (St OJ "屏鉍礎3-鑲嫦cL·鲅田锭^礎卜-绥鉍田馕*绩趄矣嫦j : * s i寸— 200927990 ❹ ❹ (s<) 備註 發明例 比較例 比較例 發明例 比較例 發明例 比較例 發明例 I比較例J 發明例 1比較例1 1發明例1 比較例 發明例 比較例 發明例 比較例 發明例 1比較例1 1 62 1比較例i 1比較例1 1比較例1 r< ^ C^3 § ΙΛ ΟΟ ΟΟ LO CO c— 53 CO oo ltd CO 拉伸特性值 TSxEl (MPa. 9〇 20034 16935 10980 20664 20306 20625 17514 22034 i 18620 19090 1 19470 20784 20550 21814 18722 20280 17220 21128 21078 16485 14688 15075 CO 卜 CNI 〇〇 crs οο CO 卜 CO oa 卜 So 卜 寸 CO CN3 CO CO 00 03 CO m CO OO CO « 8 0〇 LO Οϊ CNJ oa LO 03 1—H CO CO 05 CO C<1 03 Cs3 CO LO CO (M 03 03 <M s CD oo LO CO oa lO TS (MPa) 1113 1129 1220 1·^ CO οο CO CS3 0¾ LfD CsJ 〇〇 CO oo oo LO OD s 0¾ 另 oo LO OO OO 1299 1370 03 CO OO ΙΛ oo LO 寸 OO t—H CO oo 1112 1171 1224 m CO CO YS (MPa) 03 ι·"Η οο CO (>CJ 05 1085 οα CO CO CO iO CT> LO CO CO » h o- CO 芝 00 σ» oo LO CO CO LO LO CO CO CO OO S3 L〇 LO 卜 CO oo ΙΛ o oo CO OO CO CO CO CO 1028 ΙΛ OJ € 崩 1 1 1 1 OQ 1 I I 1 1 0Q 1 1 1 1 CP 1 1 1 1 1 Oh 回火Μ 面積率 (%) ID CO CNI ΟΟ 1 t CO C<l 呀 οα 另 男 c^> 卜 CO m 05 oa CO OJ 0^1 呀 CO 导 CO CO oo oo C£ 呀1 Μ+殘留γ 面積率 (%) C5 οα οο CT> CO Cs3 CO 04 OO τ-Η oo 卜 CO CO o»i CO <NI (Nl 0¾ ^h| F 面積率 (%) LO LO CO LO LO 呀 CO CO 03 CO § CO 写 § § § oo LO § Od LO i-H CO 05 鍍敷鋼板 No. CO <N1 <>a LO 〇ν3 CO C<J CQ 〇〇 Csl Oi C^3 CO C<l oo CO CO 寸 CO ΙΛ CO c〇 CO 〇o CO CD CO CO CO 寸 寸 黎屆瘌蜱a -赛兴隹-赛田苌劣蜱s -黎耜田璲娜S *鼙契契蟓.ί : * 6(sII90HZ.60 200927990 (實施例2) ❹ ❹ 將表6所示成分組成的鋼AA〜AL藉轉爐進行熔製，以連續 製造法作成鋼坯後’依完工溫度900°C進行熱軋為板庠 3. Omm，於壓札後以10C/s之冷卻速度進行冷卻，依 之捲取溫度予以捲取。其次，酸洗後，冷軋為板厚1.2_， 藉連續溶融鑛鋅產線，依表7所示之回火條件進行回火後， 浸潰於460°C之鍍浴中，形成附著量35〜45g/m2之鑛敷，並 於520°C進行合金化處理，依冷卻速度ιοί/秒進行冷卻， 製作鍍敷鋼板101〜130。又，如表7所示，一部分鑛敷鋼板 未進行合金化處理。然後，針對所得之鍍敷鋼板，依上述方 法測定肥粒鐵、麻田散鐵、殘留沃斯田鐵、回火麻田散鐵之 面積率及由麻田散鐵、殘留沃斯田鐵、回火麻田散鐵所形成 之第二相之平均結晶粒徑。又，於壓軋方向之直角方向上採 =JIS 5號拉伸試驗片，根據mZ2241進行拉伸試驗求 H TSxEl進一步採取I50mmxl50mm之試驗片，根據 JFST1GG1(鐵連規格）進行3次擴孔試驗而求取平均之擴孔 率λ(%) ’評價伸展凸緣性。再者，依卿專敎獻！記載 之方法’於壓軋方向之直角方向上採取平行部之寬5麵、長 7—_之猶片’以應變速度測/s進行拉伸試驗，將所測 定之應力-真應變曲線以應變量卜⑽之範圍進行積分而算 出吸收能量AE，求得AE/TS，評價财衝擊特性。刀 097140611 結果示於表8、表9。可知本發明例之鑛敷鋼板係均似 30 200927990 E12 19000MPa·%而TS-E1平衡高，擴孔率；l 250%而伸展凸 緣性優越，AE/TS2 0.063而耐衝擊特性亦優越。QS Remarks Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example Comparative Example Inventive Example Comparative Example Comparative Example Comparative Example Inventive Example Comparative Example r < 0 s § LO CO § OO CO LO oo 03 Tensile characteristic value TSxEl (MPa · %) 21440 15125 1T732 21627 16060 18630 20559 15521 | 17820 19170 1 15600 15442 20910 21114 14784 17650 19734 19470 16400 19110 21952 17450 〇〇LO OO 00 CO CO CD 00 OO c—CO OO § OO 卜 05 CD LO CO CO oo CO ιο oo s CO C^- sg 03 CO LO oa CO CM S 03 CS1 CO 03 OO 〇〇LO mm 03 CO C^J 03 OCJ s mouth<>3 CO in oa TS (MPa) o CO S CO C<l OO CO OO o CO 〇> 53 05 03 CO CD o cn> 05 1065 1040 1103 53⁄4 CO 03 〇0 but o CO o oo LO 00 LTD OO OO o oa oo ο σ> CO oo CO oo 05 CO YS (MPa) <x> oo CO s LO oo LO CO LO LO oo <NJ CO 03 CO CD LO r-HS Bu &lt ;>a CO CO oo c— OO g LO oo Lrt ΙΛ oo CD CO 03⁄4 LT> 05 CO CO ΙΛ 00 lO Micro organization t Other 1 1 CQ (X. 1 Oh 1 1 1 CQ 1 1 CU 1 1 1 1 CQ 1 1 Tempering M Area ratio (8) CO Cs3 c^- T—· OO LOl <NI inch rH O〇(Nl C<l <NI CO CO CO CNI LO CO1 CO οα C<I CvJ σο CO CO 卜 inch (Nl m residual γ area ratio (3⁄4) inch <NI r-<ID inch 05 CO eg CO CO T—< 1—«1 c〇rH 卜 LO IF area ratio (%) § C 03⁄4 iM OO C^3 in oo 〇c^- CO OO 05 in CO CO r-H CO 5S C -- OS m CO c^a 00 Plated steel plate No. 1—^ oa CO m CO c— OO 05 ο rH — CO — CO t—1 L〇CO c— OO 03 C<l (St OJ "铋基3-嫦嫦cL·鲅田锭^基卜-绥铋田馕*绩趄矣嫦j : * si inch — 200927990 ❹ ❹ (s<) Remarks Inventive Example Comparative Example Comparative Example Comparative Example Inventive Example I Comparative Example J Inventive Example 1 Comparative Example 1 1 Inventive Example 1 Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example 1 Comparative Example 1 1 62 1 Comparative Example i 1 Comparative Example 1 1 Comparative Example 1 r< ^ C^3 § ΙΛ ΟΟ ΟΟ LO CO c- 53 CO oo ltd CO Stretch Value TSxEl (MPa. 9〇20034 16935 10980 20664 20306 20625 17514 22034 i 18620 19090 1 19470 20784 20550 21814 18722 20280 17220 21128 21078 16485 14688 15075 CO BU CNI 〇〇crs οο CO 卜 CO oa 卜 So Bu CO CO3 CO CO CO CO 00 03 CO m CO OO CO « 8 0〇LO Οϊ CNJ oa LO 03 1—H CO CO 05 CO C<1 03 Cs3 CO LO CO (M 03 03 <M s CD oo LO CO oa lO TS (MPa) 1113 1129 1220 1·^ CO οο CO CS3 03⁄4 LfD CsJ 〇〇CO oo oo LO OD s 03⁄4 oo LO OO OO 1299 1370 03 CO OO ΙΛ oo LO inch OO t—H CO oo 1112 1171 1224 m CO CO YS ( MPa) 03 ι·"Η οο CO (>CJ 05 1085 οα CO CO CO iO CT> LO CO CO » h o- CO 芝 00 σ» oo LO CO CO LO LO CO CO CO OO S3 L〇LO 卜CO oo ΙΛ o oo CO OO CO CO CO CO 1028 ΙΛ OJ € Collapse 1 1 1 1 OQ 1 II 1 1 0Q 1 1 1 1 CP 1 1 1 1 1 Oh temper Μ Area ratio (%) ID CO CNI ΟΟ 1 t CO C<l 呀οα Another male c^> Bu CO m 05 oa CO OJ 0^1 呀 CO Guide CO CO oo oo C£ 呀1 Μ+residual γ Area ratio (%) C5 οα οο CT> CO Cs3 CO 04 OO τ-Η oo卜CO CO o»i CO <NI (Nl 03⁄4 ^h| F Area ratio (%) LO LO CO LO LO 呀 CO CO 03 CO § CO Write § § § oo LO § Od LO iH CO 05 Plated steel plate No CO <N1 <>a LO 〇ν3 CO C<J CQ 〇〇Csl Oi C^3 CO C<l oo CO CO 寸CO ΙΛ CO c〇CO 〇o CO CD CO CO CO蜱a -赛兴隹-赛田苌劣蜱 s - 黎耜田璲娜 S *鼙契契蟓.ί : * 6(sII90HZ.60 200927990 (Example 2) ❹ 钢 Steel AA of the composition shown in Table 6 ~AL is melted by a converter, and after being made into a slab by a continuous manufacturing method, it is hot-rolled at a temperature of 900 ° C to a plate 庠 3. Omm, and after cooling, it is cooled at a cooling rate of 10 C/s, and is wound up. The temperature is taken up. Secondly, after pickling, the cold rolling is 1.2_ thick, and the tempering condition is shown in Table 7 after tempering according to the tempering condition shown in Table 7, and then immersed in a plating bath of 460 ° C to form an adhesion amount. The ore deposit of 35 to 45 g/m2 was alloyed at 520 ° C, and cooled at a cooling rate of ιοί / sec to prepare plated steel sheets 101 to 130. Further, as shown in Table 7, a part of the mineralized steel sheet was not alloyed. Then, for the obtained plated steel sheet, the area ratio of the ferrite iron, the granulated iron, the residual Worth iron, and the tempering granulated iron was determined by the above method, and the granulated iron, the remaining Worth iron, the tempering Ma Tian The average crystal grain size of the second phase formed by the loose iron. Further, a JIS No. 5 tensile test piece was taken in the direction perpendicular to the rolling direction, and a tensile test was carried out in accordance with mZ2241 to obtain a test piece of I50 mm×150 mm further in H TSxEl, and a reaming test was performed three times according to JFST1GG1 (iron connection specification). The average hole expansion ratio λ (%) was evaluated to evaluate the stretch flangeability. In addition, Yi Qing specializes in offering! The method described is 'stretching the width of the parallel surface in the direction perpendicular to the direction of the rolling direction, taking the width of the parallel surface, the length of the 7-thickness, measuring the strain rate/s, and measuring the measured stress-true strain curve. The range of the amount (10) was integrated to calculate the absorbed energy AE, and AE/TS was obtained to evaluate the financial impact characteristics. Knife 097140611 The results are shown in Tables 8 and 9. It can be seen that the mineralized steel sheet of the present invention is similar to 30 200927990 E12 19000 MPa·% and TS-E1 has a high balance and a hole expansion ratio; l 250% and excellent stretch edge property, and AE/TS2 0.063 and excellent impact resistance.

097140611 31 200927990 備註 1 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍内 發明範圍外 發明範圍外 發明範圍外 AC3 變態點 (°C) LO oo ，···4 CO oo CO CT> oo Lf5 § ο (ΝΙ οα 00 CO CO oo CO oo oo S3 oo cn» 0¾ oo CO oo Aci 變態點 CC) 1—M <〇 T—( 卜 00 CJD CO οα 卜 卜 CO oo CO 卜 05 oo CNJ 卜 卜 成分組成(質量%) 1 1 1 1 1 1 1 0. 005 1 0.001 1 1 1 θ 1 1 1 1 1 0.003 1 1 0.002 1 1 1 CP 1 1 1 1 0.001 1 1 0.002 I 1 1 1 s 1 1 1 1 1 <Νϊ ο 1 1 1 1 1 1 1 1 1 1 CO CD 1 1 1 1 1 1 1 £ 1 i 1 CO o 1 1 1 1 1 1 1 1 1 1 οα 1 1 1 CO d g <=) 1 1 1 1 > 1 1 s ¢=5 1 1 S <=> s G> 1 1 1 1 1 1 0.02 1 1 g o' CZ5 1 s o I—H <=> 1 s c=> 1 •I-H s C5 1 1 o 〇 g <=5 1 s <=) o o’ T—H cz> 0.02 1 1 g c=> s <=> § c=? c6 另 CD s <=> g <=) 1.20 o g 〇· s c=> oo 0.005 0.002 0.010 0.004 0.003 0.001 0.007 0.004 0.005 0.006 0.004 0.003 fX 0.011 0.010 0.009 0.008 0.012 0.009 0.007 0.012 0.021 0.008 0.009 0. Oil c=> oi LO od CO r' 1 oo 1—H CM od 1—·< ΟΪ 1—H CO od <=> (Nl 3 oo CO <=> oo c=> 力 r"( o c<i <>3 o* 03 ^Η LO 1—H C=5 oo r~H in <=) (NJ 〇> o o 1—H CD g CD <=5 o* oo CD g c> 0.12 g C3 r~H 〇· s <=> 5 c? eg o <N cn 卜 200927990097140611 31 200927990 Remarks 1 Scope of the invention within the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the scope of the invention, the outside of the scope of the invention, the AC3 metamorphic point (°C), LO oo ,···4 CO oo CO CT> oo Lf5 § ο (ΝΙ οα 00 CO CO oo CO oo oo S3 oo cn» 03⁄4 oo CO oo Aci Metamorphic point CC) 1—M <〇T—( 00 CJD CO Αα Bub CO oo CO Bu 05 oo CNJ Bub composition (% by mass) 1 1 1 1 1 1 1 0. 005 1 0.001 1 1 1 θ 1 1 1 1 1 0.003 1 1 0.002 1 1 1 CP 1 1 1 1 0.001 1 1 0.002 I 1 1 1 s 1 1 1 1 1 <Νϊ ο 1 1 1 1 1 1 1 1 1 1 CO CD 1 1 1 1 1 1 1 £ 1 i 1 CO o 1 1 1 1 1 1 1 1 1 1 οα 1 1 1 CO dg <=) 1 1 1 1 > 1 1 s ¢=5 1 1 S <=> s G> 1 1 1 1 1 1 0.02 1 1 go' CZ5 1 So I—H <=> 1 sc=> 1 •IH s C5 1 1 o 〇g <=5 1 s <=) o o' T—H cz> 0.02 1 1 gc=> s <=> § c=? c6 Another CD s <=> g <=) 1.20 og 〇· sc=> oo 0.005 0.002 0.010 0. 004 0.003 0.001 0.007 0.004 0.005 0.006 0.004 0.003 fX 0.011 0.010 0.009 0.008 0.012 0.009 0.007 0.012 0.021 0.008 0.009 0. Oil c=> oi LO od CO r' 1 oo 1—H CM od 1—·< ΟΪ 1—H CO od <=> (Nl 3 oo CO <=> oo c=> Force r"( o c<i <>3 o* 03 ^Η LO 1—HC=5 oo r~H In <=) (NJ 〇> oo 1—H CD g CD <=5 o* oo CD g c> 0.12 g C3 r~H 〇· s <=> 5 c? eg o <N Cn 卜 200927990

備註 Φ 5 £ » £ * £ £ 5 發明例 £ * «=» 合金化處理 •V? 杯 你 他 +F 杯 杯 磡 m 杯 杯 Ms點 CC) eg CO 〇? ¢3¾ CO <Μ 〇〇 CO CO CD C<I οα OJ oo eg CO oa CO CsJ LO CO LO ΙΛ CO CD 寸 CO § CQ ΙΓ> 00 03 in 00 OJ LO 〇0 <ΝΙ ο <ΝΙ CO CO 5¾ (NI 00 S CO cx> § CO 00 OO CO C<I tr- φ 漤 B 再加熱 保持時間 (S) g § § § § § 导 宕 ο» C<3 S ο CO § § s § C2> a Oi ο § 宕 § s § § § § § 再加熱溫度 CC) ο 写 G> 导 Ο 写 s s ο m 寸 Ο CO oo § CO s cro CD s 〇 g ο s ο 写 〇 〇 ΙΛ eg s CO CD LO CO ο <ΝΙ 寸 o CsJ o in 寸 ο 写 § CO § CO ο 寸 〇 ο 〇 冷卻 到達溫度 ΓΟ ο οο Ο CO g CS3 <〇 s 03 o CO c? <z> o CD 卜 c=> c? Csl (NI 〇 〇 Csl <NI ο c=> s ο LO o o o CD ο CD CD § 导 CD S 03 〇 〇 eg s CZ5 OO S s s § § § g S s s s in oa LO CM ΙΛ c>a LO οα 另 〇 LO s 〇 〇 S s S § § § s § § 导 § S § § § 另 导 导 o 却 § g g § § § § 加熱 溫度 CC) ο <ΝΙ 〇ο 〇〇 oo § CO OD oo o § o oa oo Ο 0〇 c— 〇 § o 〇 CO ο 00 卜 TO 1000 § 卜 CD oo o § ο 00 CD oo 〇 § OO 另 oo ο <ΝΙ oo 00 〇 CS3 〇〇 ο 〇 § 升溫速度 (°C/s) LO C0 m S3 LD CO oo CO CO C<1 宕 卜 ΙΛ <Μ o o F~4 LO CM CO § in CM 壤 ' 窆 ω 1—1 鍵敷鋼板No. ο o CO o I in ο c〇 O s 1—H oo o σ> ο o r—1 T—« CO CO in CO 卜 T—< 00 r—l 05 t—H δ CO D— <M OO OJ 〇» 03 £ε I— 200927990 (8硌) 備註 發明例 比較例 比較例 發明例 比較例 比較例 發明例 丨比較例 「比較例1 發明例 比較例 比較例 發明例 T比較例1 比較例 比較例 比較例 1 AE/TS L 0.063 0. 048 0.062 0. 067 0.042 0.047 Oi CO CD ci 1 0.053 1 0.072 in o 0.050 0.070 0.067 LO 寸 o o 0.063 若 d 0.051 AE (MJ/m3) CO ITD ΙΛ 05 LO οα CO <NJ LO CO LO oo CNI OO CO LO 〇〇 oa CO LT3 CO r< 0 § LO in S5 LO CO C<l oo 5 CO CM m OO in 05 (NI CO oo LO 拉伸特性值 TSxEl (MPa · %) 20280 20750 20880 19404 15000 18832 20920 1 16524 ' 17170 21744 17120 21590 19648 18880 18760 14322 10240 cxa 〇 寸 (NI 1〇 οα OJ <ΝΪ (N1 03 Csl r- r—< r*"H OO CO t—( CO CD 寸 〇0 TS (MPa) LO 〇〇 C? CO oo CD οα oo oo s c— CO in oo 1046 1010 1208 1070 1270 1228 1180 1340 1023 1280 微組織’ 第二相 結晶粒徑 (μπι) 03 03 31 oi CD CM· oo p·( CNI oo LT3 r—( oi oi CNI r-H oi m lO CO oi 05 卜1 回火Μ 面積率 (%) oo r—Η CO ί—Η 呀 CM 1—H CO OO ool CO CO CM ool <NI r—H LO 00 寸 oo LO LO SSI Μ+殘留τ 面積率 (%) ID LO 卜 卜 r—<1 (Nil CN3 0¾ 00 (Nil oo F 面積率 (%) ιΛ 卜 〇〇 LO T-H LO OO (Νϊ CO LO CO ί—H 卜 oo CO LO 导 oo CO CO 寸 4 ί 鋼板 No. r*H Ο g s ?—i * < S g — 5 r-H g g ◦ i 1 1—< <>J CO r* H **"· LO CO 1 < Ε"-»—1 f-H 黎田嫦卜*银_田馐礎s*银磁餡硪d : * 寸 ε I.—I— 200927990Remarks Φ 5 £ » £ * £ £ 5 Inventive example £ * «=» Alloying treatment • V? Cup you +F cup 磡m cup Ms point CC) eg CO 〇? ¢33⁄4 CO <Μ 〇〇 CO CO CD C<I οα OJ oo eg CO oa CO CsJ LO CO LO ΙΛ CO CD inch CO § CQ ΙΓ> 00 03 in 00 OJ LO 〇0 <ΝΙ ο <ΝΙ CO CO 53⁄4 (NI 00 S CO cx&gt § CO 00 OO CO C<I tr- φ 漤B Reheat retention time (S) g § § § § § Guide 宕» C<3 S ο CO § § § § C2> a Oi ο § 宕§ s § § § § § Reheat temperature CC) ο Write G> Guide s ss ο m Ο Ο CO oo § CO s cro CD s 〇g ο s ο Write 〇〇ΙΛ eg s CO CD LO CO ο <ΝΙ inch o CsJ o in inch ο write § CO § CO ο 〇 〇 〇 cool to reach temperature ΓΟ ο οο Ο CO g CS3 <〇s 03 o CO c? <z> o CD 卜c=> c? Csl ( NI 〇〇Csl <NI ο c=> s ο LO ooo CD ο CD CD § Guide CD S 03 〇〇eg s CZ5 OO S ss § § § g S sss in oa LO CM ΙΛ c>a LO οα 〇LO s 〇 〇S s S § § § § § § § § § § Additional guidance o § gg § § § § heating temperature CC) ο <ΝΙ 〇ο 〇〇oo § CO OD oo o § o oa oo Ο 0〇c— 〇§ o 〇CO ο 00 卜 TO 1000 § 卜 CD oo o § ο 00 CD oo 〇§ OO oo oo ο <ΝΙ oo 00 〇CS3 〇〇ο 〇§ Heating rate (°C/s) LO C0 m S3 LD CO oo CO CO C<1 宕卜ΙΛ <Μ oo F~4 LO CM CO § in CM ' ' ω 1-1 bond plate No. ο o CO o I in ο c〇O s 1—H oo o σ> ο or—1 T—« CO CO in CO 卜 T—< 00 r—l 05 t—H δ CO D— <M OO OJ 〇» 03 £ε I— 200927990 ( 8 硌) Remarks Inventive Example Comparative Example Comparative Example Invention Example Comparative Example Comparative Example Invention Example Comparative Example 1 Comparative Example Comparative Example Comparative Example Inventive Example T Comparative Example 1 Comparative Example Comparative Example Comparative Example 1 AE/TS L 0.063 0 048 0.062 0. 067 0.042 0.047 Oi CO CD ci 1 0.053 1 0.072 in o 0.050 0.070 0.067 LO inch oo 0.063 if d 0.051 AE (MJ/m3) CO ITD ΙΛ 05 LO α CO <NJ LO CO LO oo CNI OO CO LO 〇〇oa CO LT3 CO r< 0 § LO in S5 LO CO C<l oo 5 CO CM m OO in 05 (NI CO oo LO tensile characteristic value TSxEl ( MPa · %) 20280 20750 20880 19404 15000 18832 20920 1 16524 ' 17170 21744 17120 21590 19648 18880 18760 14322 10240 cxa 〇 inch (NI 1〇οα OJ <ΝΪ (N1 03 Csl r- r-<r*"H OO CO t—( CO CD 〇 0 TS (MPa) LO 〇〇 C? CO oo CD οα oo oo sc— CO in oo 1046 1010 1208 1070 1270 1228 1180 1340 1023 1280 Microstructure 'Second phase crystal grain size ( Ππι) 03 03 31 oi CD CM· oo p·( CNI oo LT3 r—( oi oi CNI rH oi m lO CO oi 05 Bu 1 tempering area ratio (%) oo r—Η CO Η—Η CM CM 1 —H CO OO ool CO CO CM ool <NI r—H LO 00 inch oo LO LO SSI Μ+residual τ area ratio (%) ID LO 卜卜r—<1 (Nil CN3 03⁄4 00 (Nil oo F area Rate (%) ιΛ 〇〇 〇〇 LO TH LO OO (Νϊ CO LO CO ί—H oo CO LO Guide oo CO CO inch 4 ί Plate No. r*H Ο gs ?—i * < S g — 5 rH Gg ◦ i 1 1—<<> J CO r* H **"· LO CO 1 <Ε"-»-1 f-H 黎田嫦卜*银_田馐基础 s*银磁充硪d : * inch ε I.—I— 200927990

(6 5 備註 發明例 比較例 比較例 比較例 發明例 比較例 發明例 比較例 發明例 比較例 比較例 比較例 比較例 AE/TS j 0.069 LO LO d 0.065 os CO o <z> 0.071 0. 053 0.071 CO CD Ο 寸 CO o »*·Η g ¢=5 0. 047 (Nl <〇 CD 0.049 ^ | 1—1 LO LO 寸 CO LO CO CO LO 厂·< CD 产丨· CO LO in Οί Γ*~ < CO ι—Η LO CO 〇〇 (ΝΪ OO CNI 0¾ CO LO CO CO CO CO Cvl oo LO CJ5 οο CO CO CO iH TSxEl (MPa · %) 20776 21025 17325 20098 21504 21890 19290 19980 21758 17062 15124 ! 13287 1 19359 Si s 8 〇〇 (NI CD <NI LO CO C<J 1—M c<l CM <NJ LTD 1—< LO CO <>3 03 ΟΟ CO CO 呀 TS (MPa) οα LO (NI 卜 CO 05 CO CO 卜 1024 lO C73 1286 1332 CO 呀 05 OO 03 OO οο 05 CO 另 卜 卜 微組織^ 第二相 結晶粒徑 (/zm) <=> (Νϊ col CO oi 03 col col 卜 LO od 卜 od m c<i LO τ~Η CO <NI CO 回火Μ 面積率 (%) ι—Η 1—^ t-H oa| Ί H oa cn 1—< CO ι—H CO CO ΙΛ CO 〇〇ι OOl CD Μ+殘留γ 面積率 ⑻ 寸 寸 一 1 oai ......<| 卜 CO oo OOl 1—<1 卜 j (Nil 〇α| CO F 面積率 (%) LO oo LO OO LO oo co oo LO CO CO § ς〇 § § LO i ί ^ oo r— cr> r-H 宕 H C<J 1 t CNI (Nl CO CO LO C<J t-H CO <NI 1 M 卜 οα 1—Η ΟΟ C<l 1—» 05 CV3 o CO r—t >οε 11902/,60(6 5 Remarks Inventive Example Comparative Example Comparative Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Inventive Example Comparative Example Comparative Example Comparative Example Comparative Example AE/TS j 0.069 LO LO d 0.065 os CO o <z> 0.071 0. 053 0.071 CO CD Ο inch CO o »*·Η g ¢=5 0. 047 (Nl <〇CD 0.049 ^ | 1-1 LO LO inch CO LO CO CO LO plant·< CD 丨· CO LO in Οί Γ*~ < CO ι—Η LO CO 〇〇(ΝΪ OO CNI 03⁄4 CO LO CO CO CO CO Cvl oo LO CJ5 οο CO CO CO iH TSxEl (MPa · %) 20776 21025 17325 20098 21504 21890 19290 19980 21758 17062 15124 13287 1 19359 Si s 8 〇〇(NI CD <NI LO CO C<J 1—M c<l CM <NJ LTD 1—< LO CO <>3 03 ΟΟ CO CO 呀 TS (MPa ) οα LO (NI 卜 CO 05 CO CO 1024 lO C73 1286 1332 CO 呀 05 OO 03 OO οο 05 CO 卜卜微组织^ Second phase crystal grain size (/zm) <=> (Νϊ col CO Oi 03 col col 卜 LO od od m c<i LO τ~Η CO <NI CO tempering area area ratio (%) ι—Η 1—^ tH oa| Ί H oa cn 1—< CO ι— H CO CO ΙΛ CO 〇〇ι OOl CD Μ+residual γ area ratio (8) inch inch 1 oai ......<| 卜CO oo OOl 1—<1 卜j (Nil 〇α| CO F area ratio (%) LO oo LO OO LO oo co Oo LO CO CO § ς〇§ § LO i ί ^ oo r- cr> rH 宕H C<J 1 t CNI (Nl CO CO LO C<J tH CO <NI 1 M οα 1 - Η ΟΟ C< l 1—» 05 CV3 o CO r—t >οε 11902/,60

Claims (1)

200927990 七、申請專利範圍： 1. 一種加工性優異之高強度熔融鍍鋅鋼板，其具有以質量 %计含有 C: 0.05〜0.3%、Si : 0.0卜2. 5%、Μη: 0.5〜3.5%、p : ' 〇· 003〜〇· 100%、S : 〇. 02%以下、Α1 : 〇. 〇1〇〜1. 5%、Ν : 0. 007% ~ 以下，剩餘部為Fe及不可避免之雜質的成分組成，且具有 以面積率計含有肥粒鐵20〜87%、麻田散鐵與殘留沃斯田鐵 合計3〜10%、回火麻田散鐵10〜60%的微組織。 ® 2•如中請專利範圍第1項之加工性優異之高強度熔融鍵 鋅鋼板，其中，進一步以質量％計含有選自Cr: 〇. 〇〇5~2· _、Mo : 〇. 〇〇5〜2.嶋、v : 〇.嶋〜2.嶋、化： 〇· 005〜2. 〇〇%、Cu : 〇· 〇〇5〜2. 00%的至少 1 種元素。 3.汝申明專利範圍第^或2項之加工性優異之高強度熔融 鍍辞鋼板，其中，進一步以質量％計含有選自Ti : 。.^^^(^、^••(^(^叫^⑽的至少丨種元素。 B 4.如申請專利範圍第項# —項之加工性優異之高 強度熔融鍍鋅鋼板，其中，進一步以質量％計含有β : 〇· 0002〜〇. 005%。 5.如申請專利範圍第任一項之加工性優異之高 強度炫融鐘鋅鋼板，其中，進一步以質量％計含有選自^ 〇. _~〇篇％、腿：〇· _〜〇.咖的至少！種元素。 6.如申請專利範圍第項中任一項之加工性優異〇 強度熔融鐘鋅鋼板，其中，鑛鋅為合金化鑛辞。 ^ 097140611 36 200927990 7· —種加工性優異之高強度熔融鍍辞鋼板之製造方法，係 將具有㈣專利範圍第丨至5項中任一項之成分組成之鋼述 施打熱軋、冷軋而作成冷乳她，以對上述冷軋鋼板進行加 熱至750〜95(rc之溫度區域並保持l〇S以上後，自了抓以 10口S以上之平均冷卻速度冷卻至（H⑽。C)〜⑽點 -200 C)之溫度區域’再加熱至35Q.k溫度區域並保 持1 6QGs之條件而實施回火後，施行炼融鐵辞。 二ΓΠ利範圍第7項之加工性優異之高強度_ 辞鋼板之製造枝，其中，於施行㈣简後，施行錄鋅之 合金化處理。 9. -種加工性及耐衝擊特性優異之高強度溶 板，其具有以曾10/4 Μ 板具具有質量/。叶含有「〇〇5~〇3%^:〇.〇卜 Μη . 0. 5 3. 5% ’ p : 〇. _〜〇_ 娜；s : 〇.。找以。. ❹ 0·0ΗΜ·5%;選自Ti、肋及v之至少X 0.01〜0.2%;剩餘部為 免 兀素〇计 4 Fe及不可避免之雜質的成分組成；且 具有以面積率計含有肥粒鐵187%、細散鐵與殘留 田鐵合計3〜10%、回、μ ^ ! A fin0/ 口***田散鐵10’/◦’而上述含有麻田散 鐵與殘留沃斯田鐵I Μ楚 織輿回火麻田散鐵的第二相之平均結晶粒 徑為3απι以下的微奴織。 10. 如申清專利範固第9項之加讀及耐衝擊特性優異之 高強度溶融錄鋅鋼被，其中，進-步以質量％計含有選自 097140611 37 200927990 Cu ·· 0. 005〜2. 00%的至少丨種元素。 •如申π專利範圍第9或項之加ι性及耐衝擊特性優 異之高強度熔融鑛鋅鋼板，其中，進一步以質量％計含有β : - 0·0002〜0.005%。 、12_如申料利範圍第9至Η項中任-項之加讀及耐衝 擊特性優異之高強度炼融鑛鋅鋼板，其中，進-步以質量％ 汁含有選自Ca: 〇.·0.顏、_: 0.001〜0.005%的至少 ❹ 1種元素。 13.如申請專利_第9至12項中任—項之加讀及耐衝 擊特性優異之高強纽_鋅鋼板，其中，鍍鋅為合金化鍍 辞。 裡加上贼耐衝擊特性優異之高強度熔融鑛辞鋼板 之製造方法，係將具有中請專利範圍第9至β項中任一項 之成純成之娜施倾軋、冷軋㈣成冷軋練， ❹述冷乳鋼板於5〇〇〇C如變態點之溫度區域依HTC/s以上 之平均升溫速度進行升温，加熱至變態點〜（Ac3變態點 +30C)之溫度區域並保持1()s以上後，以呢,s以上 ，均冷卻速度冷卻至（Ms點]0(rcMMs點.。㈡之 、域，再加熱至350省C之溫度區域並保持卜刪s之^ 而實施回火後，施行熔融鍍鋅。 、 15·如申請專利範圍第14項之加讀及耐衝擊特性優異 之高強度熔雜鋅鋼板之製造方法，其中，於施行熔融錢辞 097140611 38 200927990 後，實施鍍鋅之合金化處理。200927990 VII. Patent application scope: 1. A high-strength hot-dip galvanized steel sheet having excellent workability, containing C: 0.05 to 0.3% by mass, Si: 0.0, 2.5%, Μη: 0.5 to 3.5% , p : ' 〇 · 003 ~ 〇 · 100%, S : 〇. 02% or less, Α 1 : 〇. 〇1〇~1. 5%, Ν : 0. 007% ~ below, the remaining part is Fe and inevitable The composition of the impurities is such that it contains 20 to 87% of the ferrite iron in an area ratio, 3 to 10% of the total amount of the granulated iron and the residual Worth iron, and 10 to 60% of the tempered granulated iron. ® 2 • A high-strength molten zinc-plated steel sheet having excellent workability as in the first paragraph of the patent range, wherein further contained in mass% is selected from the group consisting of Cr: 〇. 〇〇5~2· _, Mo: 〇. 〇 〇5~2.嶋, v: 〇.嶋~2. 嶋, :: 〇· 005~2. 〇〇%, Cu: 〇· 〇〇5~2. 00% of at least 1 element. 3. A high-strength molten plated steel sheet having excellent workability according to the second or second aspect of the patent, wherein the steel sheet is further selected from the group consisting of Ti: by mass%. .^^^(^,^••(^(^)^(10) at least the element of the element. B 4. The high-strength hot-dip galvanized steel sheet with excellent workability as in the scope of the patent application No. 5% by mass. 5% 5% 。 0002 0002 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. 5. _. _~〇篇%, legs: 〇· _~〇. At least the elements of the coffee! 6. The processing property is excellent as in any one of the scope of the patent application, the strength of the melting bell zinc steel plate, wherein the mineral zinc It is an alloying mineral. ^ 097140611 36 200927990 7· A method for manufacturing a high-strength molten-plated steel sheet with excellent workability, which is a steel having the composition of any of the four (4) patent scopes. Hot-rolling, cold-rolling to make cold milk, to heat the above-mentioned cold-rolled steel plate to 750~95 (the temperature range of rc and keep l〇S or more, after cooling with an average cooling rate of 10 S or more To (H(10).C)~(10) point-200 C) temperature zone 'reheat to 35Q.k temperature zone and protect After the tempering of the conditions of 6QGs, the smelting iron is applied. The high strength of the processing of the seventh item of the second profit range _ The manufacturing of the steel plate, in which the zinc alloy is applied after the implementation of (4) 9. High-strength solvent plate with excellent workability and impact resistance, which has a quality of 10/4 Μ plate. The leaf contains "〇〇5~〇3%^:〇.〇卜Μη . 0. 5 3. 5% ' p : 〇. _~〇_ Na; s : 〇.. Finding.. ❹ 0·0ΗΜ·5%; at least X, 0.01 to 0.2 from Ti, rib and v %; the remaining part is composed of the composition of 4 Fe and unavoidable impurities; and it contains 187% of the ferrite iron in the area ratio, 3 to 10% of the fine iron and the residual field iron, back, μ ^ ! A fin0 / mouth hemp field loose iron 10 ' / ◦ ' and the above-mentioned second phase containing the granulated iron and the residual Worth iron I Μ 舆 舆 舆 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻 麻Micro-nave weaving 10. If the application of the patent is the 9th item of the patent, and the high-strength molten zinc-plated steel with excellent impact resistance, the step-by-step quality is included in the selection of 09. 7140611 37 200927990 Cu ·· 0. 005~2. 00% of at least 丨 kinds of elements. ・High-strength molten zinc-zinc steel plate with excellent ι and impact resistance characteristics according to ninth or ninth patent of π patent, among which, further In the mass%, β: - 0·0002~0.005% is included. 12, such as the high-strength smelting zinc-zinc steel plate with excellent reading resistance and excellent impact resistance, in the range of items 9 to 申The step-by-step mass % juice contains at least one element selected from the group consisting of Ca: 〇.·0. 颜, _: 0.001 to 0.005%. 13. A high-strength NZ-zinc steel plate with excellent reading resistance and excellent impact resistance as claimed in the patent application _9 to 12, wherein galvanizing is alloying plating. The method for manufacturing a high-strength molten ore plate with excellent impact resistance characteristics of the thief is to be purely formed by any of the ninth to the beta items of the patent scope, and the cold rolling (four) is cooled. After rolling, the cold milk steel plate is heated at a temperature range of 5 〇〇〇C such as the metamorphic point according to the average heating rate above HTC/s, and heated to a temperature region of the metamorphic point ~ (Ac3 metamorphic point + 30 C) and maintained at 1 After () s or more, for more than s, the cooling rate is cooled to (Ms point) 0 (rcMMs point. (2), the domain, and then heated to the temperature zone of 350 province C and keep the s After tempering, hot-dip galvanizing is carried out. 15. If the application of the patent application is in the 14th item and the high-strength fused zinc-steel plate is excellent in impact resistance, after the execution of the melt money 097140611 38 200927990, The alloying treatment of galvanizing is carried out. 097140611 39 200927990 四、指定代表圖： (一) 本案指定代表圖為：無 (二) 本代表圖之元件符號簡單說明： 無 ❹ 五、本案若有化學式時，請揭示最能顯示發明特徵的化學式： 無 〇 097140611097140611 39 200927990 IV. Designated representative map: (1) The representative representative of the case is: No (2) The symbol of the symbol of the representative figure is simple: Nothing. 5. If there is a chemical formula in this case, please disclose the chemical formula that best shows the characteristics of the invention. : 无〇097140611
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